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Search Results (1,496)

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17 pages, 12008 KiB  
Article
Analysis of Tool Wear in Finish Turning of Titanium Alloy Ti-6Al-4V Under Minimum Quantity Lubrication Conditions Observed with Recurrence Quantification Analysis
by Joanna Lisowicz, Krzysztof Krupa, Kamil Leksycki, Rafał Rusinek and Szymon Wojciechowski
Materials 2025, 18(1), 79; https://doi.org/10.3390/ma18010079 (registering DOI) - 27 Dec 2024
Viewed by 273
Abstract
Titanium alloys, particularly Ti-6Al-4V, are widely used in many industries due to their high strength, low density, and corrosion resistance. However, machining these materials is challenging due to high strength at elevated temperatures, low thermal conductivity, and high chemical reactivity. This study investigates [...] Read more.
Titanium alloys, particularly Ti-6Al-4V, are widely used in many industries due to their high strength, low density, and corrosion resistance. However, machining these materials is challenging due to high strength at elevated temperatures, low thermal conductivity, and high chemical reactivity. This study investigates Recurrence Plot (RP) and Recurrence Quantification Analysis (RQA) to analyze tool wear during the finish turning of Ti-6Al-4V. The tests were conducted under Minimum Quantity Lubrication (MQL). Three inserts (two coated, one uncoated) were tested, and tool life was evaluated based on material removal volume. The issue of tool exploitation and process reliability is crucial, as it directly impacts machining performance. Results show that the uncoated insert outperformed the coated ones. RQA parameters indicated a stable-to-unstable transition in coated inserts but not in the uncoated insert. This suggests that recurrence analysis can monitor cutting dynamics in coated insert machining, but further research is needed for uncoated tools. This paper’s novelty lies in applying RP and RQA to diagnose tool wear in titanium alloy machining under MQL conditions, a method not previously explored in this context. Full article
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<p>Number of journal articles containing the keyword “recurrence plot”, divided into scientific fields, published from 1980 to 2024 (based on data from Lens.org).</p>
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<p>Number of journal articles using recurrence techniques for the analysis of the cutting process, divided by machined material, published from 2000 to 2024 (based on data from Lens.org).</p>
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<p>Workstation—NEF 600 lathe with MQL system.</p>
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<p>Record of cutting force components during turning on the example of cutting insert C.</p>
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<p>Mean value of cutting force components in the function of the volume of removed material for (<b>a</b>) cutting insert A, (<b>b</b>) cutting insert B, and (<b>c</b>) cutting insert C.</p>
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<p>Images of (<b>a</b>) cutting insert A, (<b>b</b>) cutting insert B, and (<b>c</b>) cutting insert C after achieving the tool wear criterion (point 3 in <a href="#materials-18-00079-f005" class="html-fig">Figure 5</a>).</p>
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<p>Volume of removed material for each cutting insert.</p>
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<p>Unthreshold recurrence plots for subsequent stages of tool wear.</p>
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<p>RQA parameters on the basis of analysis of the records of main cutting force component <span class="html-italic">F<sub>c</sub></span> for (<b>a</b>) cutting insert A, (<b>b</b>) cutting insert B, and (<b>c</b>) cutting insert C.</p>
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<p>RQA parameters on the basis of analysis of the records of main cutting force component <span class="html-italic">F<sub>p</sub></span> for (<b>a</b>) cutting insert A, (<b>b</b>) cutting insert B, and (<b>c</b>) cutting insert C.</p>
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<p>RQA parameters on the basis of analysis of the records of main cutting force component <span class="html-italic">F<sub>f</sub></span> for (<b>a</b>) cutting insert A, (<b>b</b>) cutting insert B, and (<b>c</b>) cutting insert C.</p>
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<p>Comparison of selected RQA parameters determined on the basis of the recording of passive force for stable machining (point 1 in <a href="#materials-18-00079-f005" class="html-fig">Figure 5</a>) and for the end of machining (point 3 in <a href="#materials-18-00079-f005" class="html-fig">Figure 5</a>).</p>
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<p>Comparison of selected RQA parameters determined on the basis of the recording of feed force for stable machining (point 1 in <a href="#materials-18-00079-f005" class="html-fig">Figure 5</a>) and for the end of machining (point 3 in <a href="#materials-18-00079-f005" class="html-fig">Figure 5</a>).</p>
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16 pages, 17228 KiB  
Article
Microstructure and Corrosion Resistance of Laser-Cladded FeCo1.5CrNi1.5Ti0.5 High-Entropy Alloy Coatings
by Sui Wang, Siqi Tian, Renjie Liu, Dengya Chen, Chao Wang, Jing Li and Sen Yang
Coatings 2024, 14(12), 1608; https://doi.org/10.3390/coatings14121608 - 23 Dec 2024
Viewed by 393
Abstract
Due to their excellent mechanical properties and corrosion resistance, high-entropy alloys (HEAs) have the potential to be used as new engineering structures and functional materials. In this study, an FeCo1.5CrNi1.5Ti0.5HEA coating was prepared on the surface of [...] Read more.
Due to their excellent mechanical properties and corrosion resistance, high-entropy alloys (HEAs) have the potential to be used as new engineering structures and functional materials. In this study, an FeCo1.5CrNi1.5Ti0.5HEA coating was prepared on the surface of a 1Cr18Ni9Ti alloy by laser cladding technology. Phase structure and microstructure were characterized by XRD and using an SEM. The corrosion resistance was evaluated by an electrochemical workstation, and the polarization curves were obtained in simulated seawater and 3.5 wt.% NaCl and 5% HCl solutions. The corrosion morphology of the Fe-based HEA coating was further characterized using the SEM, super depth of field observation, and 3D topological images. The results showed that the Fe-based HEA coating had a single-phase FCC structure with a grain size of about 10.7 ± 0.25 μM. Electrochemical analysis results showed that the corrosion resistance of the current Fe-based HEA coating was poor in HCl solutions. However, it exhibited good corrosion properties in simulated seawater and 3.5 wt.% NaCl solutions. Further analysis of the corrosion morphology revealed that in simulated seawater and the 3.5 wt.% NaCl solution, the surface of the current Fe-based HEA coating exhibited a preferential corrosion tendency between dendrites, while in the 5% HCl solution, it exhibited more obvious pitting characteristics. The results indicate that the current Fe-based HEA coating exhibits good comprehensive performance, especially in an acidic Cl corrosion environment. These findings provide a reference for the application of laser cladding prepared Fe HEA coatings. Full article
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<p>The coating sample and the XRD pattern. (<b>a</b>) The macroscopic sample prepared by laser cladding; the inset shows the OM of the lateral surface of the coating; (<b>b</b>) the XRD pattern of FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA powder and coating.</p>
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<p>Microstructure of FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating at different multiples: (<b>a</b>) 2000×; (<b>b</b>) 5000×.</p>
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<p>SEM image and the corresponding elemental distribution maps of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating.</p>
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<p>OCP and polarization curves of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate at normal temperature under different working conditions: (<b>a</b>) OCP curves; (<b>b</b>) simulated seawater; (<b>c</b>) 3.5 wt.% NaCl solution; (<b>d</b>) 5% HCl solution.</p>
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<p>EIS results and equivalent circuits of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating in simulated seawater, a 3.5 wt.% NaCl solution, and a 5% HCl solution. (<b>a</b>) Nyquist plots; (<b>b</b>) Bode plots; (<b>c</b>) the equivalent circuit used for simulated seawater and the 3.5 wt.% NaCl solution; (<b>d</b>) the equivalent circuit used for the 5% HCl solution.</p>
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<p>Micrographs and the corresponding 3D topological images of FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in simulated seawater. (<b>a</b>) Super-depth morphology of the HEA coating; (<b>b</b>) 3D topological image of the HEA coating; (<b>c</b>) super-depth morphology of the metal substrate; (<b>d</b>) 3D topological image of the metal substrate.</p>
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<p>Micrographs and the corresponding 3D topological images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in a 3.5 wt.% NaCl solution. (<b>a</b>) Super-depth morphology of the HEA coating; (<b>b</b>) 3D topological image of the HEA coating; (<b>c</b>) super-depth morphology of the metal substrate; (<b>d</b>) 3D topological image of the metal substrate.</p>
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<p>Micrographs and the corresponding 3D topological images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in a 3.5 wt.% NaCl solution. (<b>a</b>) Super-depth morphology of the HEA coating; (<b>b</b>) 3D topological image of the HEA coating; (<b>c</b>) super-depth morphology of the metal substrate; (<b>d</b>) 3D topological image of the metal substrate.</p>
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<p>Micrographs and the corresponding 3D topological images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in a 5% HCl solution. (<b>a</b>) Super-depth morphology of the HEA coating; (<b>b</b>) 3D topological image of the HEA coating; (<b>c</b>) super-depth morphology of the metal substrate; (<b>d</b>) 3D topological image of the metal substrate.</p>
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<p>SEM images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in simulated seawater. (<b>a</b>) HEA coating, 500×; (<b>b</b>) HEA coating, 2000×; (<b>c</b>) the metal substrate, 500×; (<b>d</b>) the metal substrate, 2000×.</p>
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<p>SEM images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in a 3.5 wt.% NaCl solution. (<b>a</b>) HEA coating, 500×; (<b>b</b>) HEA coating, 2000×; (<b>c</b>) the metal substrate, 500×; (<b>d</b>) the metal substrate, 2000×.</p>
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<p>SEM images of the FeCo<sub>1.5</sub>CrNi<sub>1.5</sub>Ti<sub>0.5</sub> HEA coating and the metal substrate after electrochemical testing in a 5% HCl solution. (<b>a</b>) HEA coating, 500×; (<b>b</b>) HEA coating, 2000×; (<b>c</b>) the metal substrate, 500×; (<b>d</b>) the metal substrate, 2000×.</p>
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16 pages, 7065 KiB  
Article
Hot Deformation Behavior of Electron-Beam Cold-Hearth Melted Ti-6Al-4V Alloy
by Weiju Jia, Chengliang Mao and Wei Zhou
Metals 2024, 14(12), 1459; https://doi.org/10.3390/met14121459 - 20 Dec 2024
Viewed by 351
Abstract
The deformation behavior and microstructure changes of electron-beam cold-hearth-melted (EBCHM) Ti-6Al-4V alloy were investigated. The stress–strain curves of the alloy were obtained, the constitutive model was established based on the Arrhenius equation, and the hot processing map was drawn. The results showed that [...] Read more.
The deformation behavior and microstructure changes of electron-beam cold-hearth-melted (EBCHM) Ti-6Al-4V alloy were investigated. The stress–strain curves of the alloy were obtained, the constitutive model was established based on the Arrhenius equation, and the hot processing map was drawn. The results showed that the stress of the alloy decreases with increasing temperature and decreasing strain rate. In the β phase field, there are more recrystallized grains when the strain rate is slow, and the recrystallization of the β phase does not have enough time to occur when the strain rate is fast. There are obvious shear bands in the microstructure at the strain rate of 10 s−1. In the α + β field, the morphology and crystallographic orientation of the microstructure changed simultaneously. Globularization is a typical microstructure evolution characteristic. The prismatic slip is easier to activate than basal and pyramidal slips. Moreover, globularization of the lamellar α phase is not synchronously crystallographic and morphological. Full article
(This article belongs to the Special Issue Structure and Mechanical Properties of Titanium Alloys)
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<p>Initial microstructures of the EBCHM Ti-6Al-4V alloy.</p>
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<p>The stress–strain curves of the EBCHM Ti-6Al-4V alloy deformed at different temperatures: (<b>a</b>) 910 °C, (<b>b</b>) 970 °C, (<b>c</b>) 1030 °C, and (<b>d</b>) 1060 °C.</p>
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<p>Linear fitting ln<math display="inline"><semantics> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> </semantics></math>-lnσ diagram of the EBCHM Ti-6Al-4V alloy using the peak values of flow stresses under different deformation conditions.</p>
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<p>Linear fitting ln<math display="inline"><semantics> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> </semantics></math>-σ diagram of the EBCHM Ti-6Al-4V alloy using the peak values of flow stresses under different deformation conditions.</p>
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<p>Linear fitting ln<math display="inline"><semantics> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> </semantics></math>-ln[sinh(ασ)] diagram of EBCHM Ti-6Al-4V alloy using the peak values of flow stresses under different deformation conditions.</p>
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<p>Linear fitting ln[sinh(ασ)]-1/T diagram of the EBCHM Ti-6Al-4V alloy using the peak values of flow stresses under different deformation conditions.</p>
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<p>Linear fitting ln[sinh(ασ)]-1/T diagram of the EBCHM Ti-6Al-4V alloy using the peak values of flow stresses under different deformation conditions.</p>
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<p>Processing map of the EBCHM Ti-6Al-4V alloy with the true strain of 0.8.</p>
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<p>Microstructure characteristics under the deformation condition of the single β phase field: (<b>a</b>) 1030 °C/0.001 s<sup>−1</sup>, (<b>b</b>) 1030 °C/0.1 s<sup>−1</sup>, and (<b>c</b>) 1030 °C/10 s<sup>−1</sup>.</p>
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<p>Euler + band contrast (BC) map, inverse pole figures (IPF), and pole figures (PF) of the microstructure at 910 °C: (<b>a1</b>) Euler + BC at a strain rate of 0.001 s<sup>−1</sup>, (<b>a2</b>) IPF at a strain rate of 0.001 s<sup>−1</sup>, (<b>a3</b>) PF at a strain rate of 0.001 s<sup>−1</sup>, (<b>b1</b>) Euler + BC at a strain rate of 1 s<sup>−1</sup>, (<b>b2</b>) IPF at a strain rate of 1 s<sup>−1</sup>, (<b>b3</b>) PF at a strain rate of 1 s<sup>−1</sup>, (<b>c1</b>) Euler + BC at a strain rate of 10 s<sup>−1</sup>, (<b>c2</b>) IPF at a strain rate of 10 s<sup>−1</sup>, and (<b>c3</b>) PF at a strain rate of 10 s<sup>−1</sup>.</p>
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<p>Euler + band contrast (BC) map, inverse pole figures (IPF), and pole figures (PF) of the microstructure at 970 °C: (<b>a1</b>) Euler + BC at a strain rate of 0.001 s<sup>−1</sup>, (<b>a2</b>) IPF at a strain rate of 0.001 s<sup>−1</sup>, (<b>a3</b>) PF at a strain rate of 0.001 s<sup>−1</sup>, (<b>b1</b>) Euler + BC at a strain rate of 1 s<sup>−1</sup>, (<b>b2</b>) IPF at a strain rate of 1 s<sup>−1</sup>, (<b>b3</b>) PF at a strain rate of 1 s<sup>−1</sup>, (<b>c1</b>) Euler + BC at a strain rate of 10 s<sup>−1</sup>, (<b>c2</b>) IPF at a strain rate of 10 s<sup>−1</sup>, and (<b>c3</b>) PF at a strain rate of 10 s<sup>−1</sup>.</p>
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<p>Schmid factor maps for different slip systems at 910 °C (<b>a</b>,<b>b</b>) and 970 °C (<b>c</b>,<b>d</b>): (<b>a1</b>) (0001)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>a2</b>) (1-100)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>a3</b>) (1-101)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>b1</b>) (0001)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>, (<b>b2</b>) (1-100)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>, (<b>b3</b>) (1-101)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>, (<b>c1</b>) (0001)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>c2</b>) (1-100)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>c3</b>) (1-101)&lt;11-20&gt; at a strain rate of 0.001 s<sup>−1</sup>, (<b>d1</b>) (0001)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>, (<b>d2</b>) (1-100)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>, and (<b>d3</b>) (1-101)&lt;11-20&gt; at a strain rate of 1 s<sup>−1</sup>.</p>
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<p>Crystallographic characteristics of the typical α phase at 970 °C/1 s<sup>−1</sup>.</p>
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21 pages, 15856 KiB  
Article
Compressive Behavior of Inconel 625 and Ti-6Al-4V Strut Lattices Fabricated by LPBF
by Mihaela Raluca Condruz, Teodor Adrian Badea and Alexandru Paraschiv
Appl. Sci. 2024, 14(24), 11909; https://doi.org/10.3390/app142411909 - 19 Dec 2024
Viewed by 435
Abstract
The present study assessed the compression performance of four strut lattices manufactured via laser powder bed fusion (LPBF), namely selective laser melting (SLM) from Inconel 625 and Ti-6Al-4V. Static finite element analysis and mechanical testing were performed, and it was concluded that the [...] Read more.
The present study assessed the compression performance of four strut lattices manufactured via laser powder bed fusion (LPBF), namely selective laser melting (SLM) from Inconel 625 and Ti-6Al-4V. Static finite element analysis and mechanical testing were performed, and it was concluded that the experimentally determined performance trend was in good agreement with that obtained by numerical methods. The cell type greatly influences the compressive performance of the lattices, regardless of the material used for manufacturing. The best compressive performances were recorded for the octet lattice, followed by the truncated octahedron, Kelvin, and re-entrant lattices. Regarding material performance, for the first maximum compressive strength, similar results were recorded for both materials; a difference was recorded in the case of yield strength, with higher values were recorded for Ti-6Al-4V compared to Inconel 625. The average first maximum compressive strength for the Ti-6Al-4V lattice was between 30.39 and 290.17 MPa, and it was within a range of 16.22–258.71 MPa for Inconel 625. The elastic modulus was between 1.74 and 4.72 GPa for Ti-6Al-4V, and 1.13 and 4.46 GPa for Inconel 625. A more ductile behavior was registered for the nickel-based superalloy than for the titanium alloy; the Inconel 625 specimens were characterized by a bending-dominant damage mode, and Ti-6Al-4V specimens were characterized more by a stretch-dominant damage mode. Full article
(This article belongs to the Section Additive Manufacturing Technologies)
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<p>Examples of 3D lattice structures using different cell designs arranged over a cubic volume (designed using nTop software, version 4.9).</p>
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<p>Representative images with sections of the designed cylindrical specimens.</p>
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<p>Representative images showcasing a comparison between manufactured Ti-6Al-4V specimens and their respective 3D CAD models.</p>
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<p>Microstructural features of stress-relieved alloys: (<b>a</b>) Inconel 625; (<b>b</b>) Ti-6Al-4V.</p>
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<p>Static finite element analysis results—von Mises stress comparison for different cell topologies (octet, truncated octahedron, Kelvin, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Static finite element analysis results—von Mises stress comparison for different cell topologies (octet, truncated octahedron, Kelvin, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Static finite element analysis results—von Mises stress comparison for different cell topologies (octet, truncated octahedron, Kelvin, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Static finite element analysis results—von Mises stress comparison for different cell topologies (octet, truncated octahedron, Kelvin, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Static finite element analysis results—von Mises stress comparison for different cell topologies (octet, truncated octahedron, Kelvin, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Static finite element analysis results—resultant displacement comparison for different cell topologies (octet, truncated octahedron, Kelvin cell, re-entrant) and materials (Inconel 625, Ti-6Al-4V).</p>
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<p>Additive-manufactured specimens during different stages of compression testing.</p>
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<p>The graphical representation of the tendency recorded in the case of the compression tests experimentally performed for all cell types and both materials.</p>
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<p>Representative stress–strain curves for all four lattices and materials used for specimens’ manufacturing.</p>
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<p>Images illustrating damaged specimens manufactured from four cell topologies and two materials: Ti-6Al-4V titanium alloy (<b>left</b>) and Inconel 625 nickel-based superalloy (<b>right</b>).</p>
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<p>The trendline of the yield strength and the von Mises stress, for Inconel 625 (<b>a</b>) and for Ti-6Al-4V (<b>b</b>).</p>
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24 pages, 13087 KiB  
Article
Enhancement of Machining Performance of Ti-6Al-4V Alloy Though Nanoparticle-Based Minimum Quantity Lubrication: Insights into Surface Roughness, Material Removal Rate, Temperature, and Tool Wear
by Tahir Mehmood and Muhammad Shahid Khalil
J. Manuf. Mater. Process. 2024, 8(6), 293; https://doi.org/10.3390/jmmp8060293 - 18 Dec 2024
Viewed by 602
Abstract
In competitive industry, economical and environmentally friendly production techniques are essential. In this sense, cleaner and more sustainable machining techniques are the industry’s focus. In addition to green methods, effective parametric control is necessary for hard-to-cut materials, particularly titanium Ti-6Al-4V, which is extensively [...] Read more.
In competitive industry, economical and environmentally friendly production techniques are essential. In this sense, cleaner and more sustainable machining techniques are the industry’s focus. In addition to green methods, effective parametric control is necessary for hard-to-cut materials, particularly titanium Ti-6Al-4V, which is extensively used in a diversity of industries, including aerospace, medical, and military applications. Therefore, the current study aims to improve the machining performance of Ti-6Al-4V alloy using sustainable lubrication conditions. The effect of Al2O3 nanoparticles based on the minimum quantity lubrication (N-MQL) condition on surface quality and productivity are compared with minimum quantity lubrication (MQL). The performance measures, including surface roughness (Ra), material removal rate (MRR), and temperature, are evaluated at three machining variables, i.e., cutting speed (Vc), feed rate (f), and depth of cut (ap). These performance measures are further assessed by tool wear and surface morphology analysis. ap, f, and Vc are the most influencing parameters for Ra, MRR, and temperature, regardless of lubrication mode. The optimized values of RA of 0.728443 µm, MRR of 2443.77 m3/min, and temperature of 337 °C are achieved at N-MQL. For the N-MQL state, the optimized values of Ra of 0.55 µm, MRR of 2579.5 m3/min, and temperature of 323.554 °C are attained through a multi-response optimization desirability approach. Surface morphology analysis reveals a smooth machined surface with no obvious surface flaws, such as feed marks and adhesion, under N-MQL conditions, which significantly enhances the surface finish of the parts. The machining performance under the N-MQL condition has been enhanced considerably in terms of an improvements in surface finish of 32.96% and MRR of 11.56%, along with a decrease in temperature (17.22%) and higher tool life (326 s) than MQL. Furthermore, Al2O3 is advised over MQL because it uses less energy and has reduced tool wear and improved surface quality, and it is a cost-effective and sustainable fluid. Full article
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Figure 1
<p>MQL machining setup: (<b>a</b>) MQL system; (<b>b</b>) Milling Process.</p>
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<p>Experimental methodology.</p>
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<p>Surface plots for Ra at MQL: (<b>a</b>) V<sub>c</sub> vs. f; (<b>b</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>c</b>) a<sub>p</sub> vs. f, At N-MQL; (<b>d</b>) V<sub>c</sub> vs. f; (<b>e</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>f</b>) a<sub>p</sub> vs. f.</p>
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<p>Surface plots for MRR at MQL: (<b>a</b>) V<sub>c</sub> vs. f; (<b>b</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>c</b>) a<sub>p</sub> vs. f, At N-MQL; (<b>d</b>) V<sub>c</sub> vs. f; (<b>e</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>f</b>) a<sub>p</sub> vs. f.</p>
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<p>Surface plots for temperature at MQL: (<b>a</b>) V<sub>c</sub> vs. f; (<b>b</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>c</b>) a<sub>p</sub> vs. f, and at N-MQL: (<b>d)</b> V<sub>c</sub> vs. f; (<b>e</b>) V<sub>c</sub> vs. a<sub>p</sub>; (<b>f</b>) a<sub>p</sub> vs. f.</p>
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<p>Variation of flank wear at different machining times.</p>
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<p>SEM images of Tool flank wear at MQL: (<b>a</b>) tool life = 100 s, flank wear = 0.15 mm; (<b>b</b>) tool life = 100 s, flank wear = 0.10 mm, and at N-MQL: (<b>c</b>) tool life = 350 s, flank wear = 0.61 mm; (<b>d</b>) tool life = 350 s, flank wear = 0.33 mm.</p>
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<p>SEM images of machined surface: (<b>a</b>–<b>c</b>) at MQL; (<b>d</b>–<b>f</b>) at N-MQL.</p>
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<p>Surface topography images: (<b>a</b>–<b>c</b>) at MQL; (<b>d</b>–<b>f</b>) at N-MQL.</p>
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<p>Improvements in machining attributes Ra, MRR, and temperature.</p>
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18 pages, 18179 KiB  
Article
Improving the Wear and Corrosion Resistance of Titanium Alloy Parts via the Deposition of DLC Coatings
by Alexander Metel, Catherine Sotova, Sergey Fyodorov, Valery Zhylinski, Vadzim Chayeuski, Filipp Milovich, Anton Seleznev, Yuri Bublikov, Kirill Makarevich and Alexey Vereschaka
C 2024, 10(4), 106; https://doi.org/10.3390/c10040106 - 16 Dec 2024
Viewed by 581
Abstract
This article compares the properties of the diamond-like carbon (DLC) coating with those of ZrN and (Zr,Hf)N coatings deposited on the Ti-6Al-4V titanium alloy substrate. To improve substrate adhesion during the deposition of the DLC coating, preliminary etching with chromium ions was conducted, [...] Read more.
This article compares the properties of the diamond-like carbon (DLC) coating with those of ZrN and (Zr,Hf)N coatings deposited on the Ti-6Al-4V titanium alloy substrate. To improve substrate adhesion during the deposition of the DLC coating, preliminary etching with chromium ions was conducted, ensuring the formation of a chromium-saturated diffusion surface layer in the substrate. A Si-DLC layer followed by a pure DLC layer was then deposited. The hardness of the coatings, their surface morphology, fracture strength in the scratch test, and tribological properties and wear resistance in the pin-on-disk test in contact with Al2O3 and steel indenters were investigated. The structure of the DLC coating was studied using transmission electron microscopy, and its corrosion resistance in an environment simulating blood plasma was also investigated. In the pin-on-disk test in contact with Al2O3 and AISI 52100 indenters, the DLC-coated sample demonstrates a much lower friction coefficient and significantly better wear resistance compared to the nitride-coated and uncoated samples. Both nitride coatings—(Zr,Hf)N and ZrN—and the DLC coating slow down the corrosive dissolution of the base compared to the uncoated sample. The corrosion currents of the (Zr,Hf)N-coated samples are 37.01 nA/cm2, 20% higher than those of the ZrN-coated samples. The application of (Zr,Hf)N, ZrN, and DLC coatings on the Ti-6Al-4V alloy significantly inhibits dissolution currents (by 30–40%) and increases polarization resistance 1.5–2.0-fold compared to the uncoated alloy in 0.9% NaCl at 40 °C. Thus, the DLC coating of the described structure simultaneously provides effective wear and corrosion resistance in an environment simulating blood plasma. This coating can be considered in the manufacture of medical products (in particular, implants) from titanium alloys, including those functioning in the human body and subject to mechanical wear (e.g., knee joint endoprostheses). Full article
(This article belongs to the Special Issue High-Performance Carbon Materials and Their Composites)
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<p>Surface morphology of (<b>a</b>,<b>b</b>) ZrN and (<b>c</b>) (Zr,Hf)N coatings; and (<b>d</b>–<b>f</b>) structural defects of the (Zr,Hf)N coating (SEM).</p>
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<p>Surface morphology of (<b>a</b>,<b>b</b>) ZrN and (<b>c</b>) (Zr,Hf)N coatings; and (<b>d</b>–<b>f</b>) structural defects of the (Zr,Hf)N coating (SEM).</p>
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<p>(<b>a</b>,<b>b</b>) Surface morphology of DLC coatings and (<b>c</b>–<b>f</b>) structural defects of the coating (SEM).</p>
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<p>(<b>a</b>,<b>b</b>) Surface morphology of DLC coatings and (<b>c</b>–<b>f</b>) structural defects of the coating (SEM).</p>
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<p>Internal structure (TEM) and elemental and phase (SAED) composition of DLC coating.</p>
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<p>Acoustic emission data (<b>top</b>) and general view of the scribing groove (<b>bottom</b>) for the (<b>a</b>) ZrN, (<b>b</b>) (Zr,Hf)N, and (<b>c</b>) DLC coatings.</p>
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<p>Acoustic emission data (<b>top</b>) and general view of the scribing groove (<b>bottom</b>) for the (<b>a</b>) ZrN, (<b>b</b>) (Zr,Hf)N, and (<b>c</b>) DLC coatings.</p>
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<p>The surface structure and nature of DLC coating destruction during scratch test: (<b>a</b>) formation of a crack in the coating structure, and (<b>b</b>) the nature of coating destruction at the boundary of the scribing groove (SEM).</p>
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<p>Appearance of wear tracks of samples after pin-on-disk testing.</p>
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<p>Tribological properties (coefficient of friction [COF]) and wear resistance in pin-on-disk tests: (<b>a</b>) COF in contact with Al<sub>2</sub>O<sub>3</sub> indenter, (<b>b</b>) COF in contact with AISI 52100 indenter, (<b>c</b>) wear dynamics in contact with Al<sub>2</sub>O<sub>3</sub> indenter, (<b>d</b>) wear dynamics in contact with AISI 52100 indenter, (<b>e</b>) mass loss of Al<sub>2</sub>O<sub>3</sub> indenter, and (<b>f</b>) mass loss of AISI 52100 indenter.</p>
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<p>Tribological properties (coefficient of friction [COF]) and wear resistance in pin-on-disk tests: (<b>a</b>) COF in contact with Al<sub>2</sub>O<sub>3</sub> indenter, (<b>b</b>) COF in contact with AISI 52100 indenter, (<b>c</b>) wear dynamics in contact with Al<sub>2</sub>O<sub>3</sub> indenter, (<b>d</b>) wear dynamics in contact with AISI 52100 indenter, (<b>e</b>) mass loss of Al<sub>2</sub>O<sub>3</sub> indenter, and (<b>f</b>) mass loss of AISI 52100 indenter.</p>
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<p>Superposition of potentiodynamic curves of the studied (Zr,Hf)N, ZrN, and DLC coatings on the surface of the Ti-6Al-4V alloy in 0.9% NaCl at 40 °C (Vp = 10 mV/s).</p>
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<p>Oxidation processes in the DLC coating surface after exposure to 0.9% NaCl at 40 °C (Vp = 10 mV/s; TEM).</p>
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23 pages, 8899 KiB  
Article
Loading Frequency Classification in Shape Memory Alloys: A Machine Learning Approach
by Dmytro Tymoshchuk, Oleh Yasniy, Pavlo Maruschak, Volodymyr Iasnii and Iryna Didych
Computers 2024, 13(12), 339; https://doi.org/10.3390/computers13120339 - 14 Dec 2024
Viewed by 471
Abstract
This paper investigates the use of machine learning methods to predict the loading frequency of shape memory alloys (SMAs) based on experimental data. SMAs, in particular nickel-titanium (NiTi) alloys, have unique properties that restore the original shape after significant deformation. The frequency of [...] Read more.
This paper investigates the use of machine learning methods to predict the loading frequency of shape memory alloys (SMAs) based on experimental data. SMAs, in particular nickel-titanium (NiTi) alloys, have unique properties that restore the original shape after significant deformation. The frequency of loading significantly affects the functional characteristics of SMAs. Experimental data were obtained from cyclic tensile tests of a 1.5 mm diameter Ni55.8Ti44.2 wire at different loading frequencies (0.1, 0.5, 1.0, and 5.0 Hz). Various machine learning methods were used to predict the loading frequency f (Hz) based on input parameters such as stress σ (MPa), number of cycles N, strain ε (%), and loading–unloading stage: boosted trees, random forest, support vector machines, k-nearest neighbors, and artificial neural networks of the MLP type. Experimental data of 100–140 load–unload cycles for four load frequencies were used for training. The dataset contained 13,365 elements. The results showed that the MLP neural network model demonstrated the highest accuracy in load frequency classification. The boosted trees and random forest models also performed well, although slightly below MLP. The SVM method also performed quite well. The KNN method showed the worst results among all models. Additional testing of the MLP model on cycles that were not included in the training data (200th, 300th, and 1035th cycles) showed that the model retains high efficiency in predicting load frequency, although the accuracy gradually decreases on later cycles due to the accumulation of structural changes in the material. Full article
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<p>The machine for the experiment: (<b>a</b>) general view of the SMT-100 machine; (<b>b</b>) Bi-02-313 sensor; (<b>c</b>) test sample fixed in the grippers.</p>
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<p>The window of the Test Builder software during the experiment.</p>
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<p>Hysteresis loops of 100–120th SMA loading and unloading cycles for a frequency of 0.1 Hz.</p>
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<p>Schematic representation of the Boosted Tree model.</p>
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<p>Schematic representation of the Random Forest model.</p>
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<p>MLP architecture with one hidden layer.</p>
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<p>Model of a neuron.</p>
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<p>Average multinomial deviance change graph depending on the number of trees in the model.</p>
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<p>Confusion matrix of the Boosted Trees model of the test data set.</p>
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<p>Misclassification rate change graph for training and test samples in the process of model training.</p>
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<p>Confusion matrix of the Random Forest model of the test data set.</p>
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<p>Confusion matrix of the SVM model of the test data set.</p>
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<p>Confusion matrix of the KNN model of the test data set.</p>
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<p>Confusion matrix of the 4-51-4 neural network of the test data set.</p>
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<p>Confusion matrix of the 4-51-4 neural network for the 200th cycle.</p>
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<p>Charts of cumulative gain in frequency classification for the 200th cycle.</p>
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<p>Performance indicators of the MLP 4-51-4 neural network for the 200th cycle.</p>
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<p>Confusion matrix of the 4-51-4 neural network for the 300th cycle.</p>
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<p>Charts of cumulative gain in frequency classification for the 300th cycle.</p>
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<p>Performance indicators of the MLP 4-51-4 neural network for the 300th cycle.</p>
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<p>Confusion matrix of the 4-51-4 neural network for the 1035th cycle.</p>
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<p>Performance indicators of the MLP 4-51-4 neural network for the 1035th cycle.</p>
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<p>Charts of cumulative gain in frequency classification for the 1035th cycle.</p>
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<p>Confidence level histograms for the test dataset (<b>a</b>), 200th cycle (<b>b</b>), 300th cycle (<b>c</b>), 1035th cycle (<b>d</b>).</p>
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19 pages, 13416 KiB  
Article
The Use of Graphite Micropowder in the Finish Turning of the Ti-6Al-4V Titanium Alloy Under Minimum Quantity Lubrication Conditions
by Joanna Lisowicz, Witold Habrat, Krzysztof Krupa, Grażyna Mrówka-Nowotnik, Paweł Szroeder, Magdalena Zawada-Michałowska and Jarosław Korpysa
Materials 2024, 17(24), 6121; https://doi.org/10.3390/ma17246121 - 14 Dec 2024
Viewed by 492
Abstract
The use of the minimum quantity lubrication (MQL) method during machining leads to the reduced consumption of cooling and lubricating liquids, thus contributing to sustainable machining. To improve the properties of liquids used under MQL conditions, they are enriched with various types of [...] Read more.
The use of the minimum quantity lubrication (MQL) method during machining leads to the reduced consumption of cooling and lubricating liquids, thus contributing to sustainable machining. To improve the properties of liquids used under MQL conditions, they are enriched with various types of micro- and nanoparticles. The purpose of this study was to investigate the effect of the addition of graphite micropowder (GMP) on tool life, cutting force components, and selected surface roughness parameters during the finish turning of the Ti-6Al-4V titanium alloy under MQL conditions. The addition of 0.6 wt% of GMP to the base liquid in machining under MQL conditions leads to an extension of tool life by 7% and 96% compared to machining with a liquid without the addition of GMP and dry machining, respectively. Mathematical models of the cutting force components and surface roughness parameters were developed, taking into account the change in cutting speed and feed. It was found that the use of a liquid with the addition of GMP extends the range of cutting parameters for which the shape of chips obtained is acceptable in terms of work safety. The novelty of this study lies in the use of a cutting fluid composed of bis(2-ethylhexyl) adipate and diester, enriched with graphite micropowder, which has not been extensively investigated for machining titanium alloys under MQL conditions. Full article
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<p>Internal cooling and lubrication liquid supply system: (<b>a</b>) tool holder, (<b>b</b>) oil mist delivery scheme.</p>
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<p>SEM images of GMP at different magnifications: (<b>a</b>) 1000×, (<b>b</b>) 50,000×, and (<b>c</b>) 200,000×; (<b>d</b>) EDX spectrum obtained from the area marked with a green rectangle with the results of the surface elemental analysis.</p>
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<p>Location of research points in the field of chip-shaping control.</p>
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<p>The structure and relationships occurring in the metrology of the surface layer of aircraft alloys after machining.</p>
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<p>Passive force as a function of the volume of material removed.</p>
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<p>Volume of material removed until the tool wear criterion was reached for dry machining and machining under MQL conditions with the use of the A3G0 and A3G60 liquids.</p>
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<p>The influence of feed and cutting speed on the (<b>a</b>) main cutting force <span class="html-italic">F<sub>c</sub></span>, (<b>b</b>) passive force <span class="html-italic">F<sub>p</sub></span>, and (<b>c</b>) feed force <span class="html-italic">F<sub>f</sub></span> in the finish turning of Ti-6Al-4V under MQL conditions with the use of the A3G0 liquid.</p>
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<p>The influence of feed and cutting speed on the (<b>a</b>) main cutting force <span class="html-italic">F<sub>c</sub></span>, (<b>b</b>) passive force <span class="html-italic">F<sub>p</sub></span>, (<b>c</b>) feed force <span class="html-italic">F<sub>f</sub></span> in the finish turning of Ti-6Al-4V in MQL conditions with the use of the A3G60 liquid.</p>
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<p>Changes in values of the (<b>a</b>) main cutting force <span class="html-italic">F<sub>c</sub></span>, (<b>b</b>) passive force <span class="html-italic">F<sub>p</sub></span>, and (<b>c</b>) feed force <span class="html-italic">F<sub>f</sub></span> due to the addition of graphite micropowder to the base liquid in comparison to machining with a liquid without graphite micropowder.</p>
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<p>The influence of feed and cutting speed on the surface roughness parameters (<b>a</b>) <span class="html-italic">Sa</span> and (<b>b</b>) <span class="html-italic">Sz</span>, measured after the finish turning of Ti-6Al-4V under MQL conditions with the use of the A3G0 liquid.</p>
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<p>The influence of feed and cutting speed on the surface roughness parameters (<b>a</b>) <span class="html-italic">Sa</span> and (<b>b</b>) <span class="html-italic">Sz</span>, measured after the finish turning of Ti-6Al-4V under MQL conditions with the use of the A3G60 liquid.</p>
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<p>Changes in the values of surface roughness parameters (<b>a</b>) <span class="html-italic">Sa</span> and (<b>b</b>) <span class="html-italic">Sz</span> due to the addition of graphite micropowder to the base liquid in comparison to machining with a liquid without graphite micropowder.</p>
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<p>Chip shapes when finish turning Ti-6Al-4V.</p>
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<p>Examples of microstructures after (<b>a</b>) turning under MQL conditions without an additive, (<b>b</b>) turning under MQL conditions with the addition of 0.6 wt% of graphite micropowder, and (<b>c</b>) dry turning.</p>
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15 pages, 7940 KiB  
Article
Study on Fatigue Behavior and Fracture Mechanism of LMD Ti-6.5Al-3.5Mo-1.5Zr-0.3Si Alloy Based on Microstructure
by Yuxue Wu, Yongxin Wang, Yunmei Lu and Chenxi Zhao
Materials 2024, 17(24), 6112; https://doi.org/10.3390/ma17246112 - 13 Dec 2024
Viewed by 460
Abstract
This study explores the fatigue behavior and fracture mechanisms of TC11 titanium alloy formed by laser metal deposition (LMD) and subjected to double annealing. The research focuses on how the alloy’s unique microstructure, consisting of alternating equiaxed and columnar crystals, influences its fatigue [...] Read more.
This study explores the fatigue behavior and fracture mechanisms of TC11 titanium alloy formed by laser metal deposition (LMD) and subjected to double annealing. The research focuses on how the alloy’s unique microstructure, consisting of alternating equiaxed and columnar crystals, influences its fatigue performance. The microstructure’s basket-like α’ phase, made up of both plate-shaped and needle-like structures, leads to variations in crack growth behavior, as shown in the relationship between the crack growth rate and the stress intensity. An analysis of slip patterns reveals that equiaxed crystals undergo more frequent deformation, accelerating crack propagation compared to the more evenly distributed deformation in columnar crystals. These findings suggest a new approach for improving the fatigue resistance of 3D-printed titanium alloys by optimizing their microstructure. This study provides valuable insights for enhancing material toughness and extending the lifespan of titanium alloys in applications such as aerospace and biomedical engineering. Full article
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<p>Heat treatment process of deposited specimen.</p>
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<p>(<b>a</b>) Schematic illustration of the deposition direction. Schematic representation of specimens: (<b>b1</b>) Fatigue crack extension specimen, (<b>b2</b>) Fatigue tensile specimen.</p>
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<p>Fitting diagram of S-N curves in two different forming directions of Kt = 1 and Kt = 3.</p>
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<p>T1 sample crack source morphology (<b>a</b>); dimple morphology (<b>a1</b>); stable propagation zone morphology (<b>a2</b>); T2 sample crack source morphology (<b>b</b>); dimple morphology (<b>b1</b>); stable propagation zone morphology (<b>b2</b>).</p>
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<p>Schematic representation of the fatigue tensile fracture location (<b>a</b>); schematic representation of the wire-cut sampling (<b>b</b>); schematic representation of the macroscopic micro-morphology of the sample (<b>c</b>).</p>
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<p>Partial SEM diagrams of T1 (<b>a</b>) and T2 (<b>b</b>) crack propagation path.</p>
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<p>Columnar crystal region Euler diagram (<b>a</b>) and its corresponding orientation difference diagram (<b>c</b>) and equiaxed crystal region Euler diagram (<b>b</b>) and its corresponding orientation difference diagram(<b>d</b>).</p>
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<p>SEM diagrams of grain boundaries and secondary cracks along the crack propagation path. (a,b) Equiaxed and columnar grain boundary morphology (c) Secondary crack.</p>
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<p>Metallographic structure diagram of the boundary area between the equiaxed crystals and columnar crystals (<b>a</b>). 200 times metallographic structure diagram (<b>b</b>). Internal metallographic structure diagram of grains (<b>c</b>).</p>
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<p>Schematic diagram of fatigue crack growth path in L-T direction (<b>a</b>) and T-L direction (<b>b</b>).</p>
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<p>da/dN~ΔK diagram (<b>a</b>) and da/dN~a diagram (<b>b</b>) of L-T and T-L crack propagation specimens.</p>
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<p>Columnar intracrystalline IPF pattern (<b>a</b>). Polar pattern α (<b>a1</b>) β (<b>a2</b>) and equiaxed intracrystalline IPF pattern (<b>b</b>). Polar pattern α (<b>b1</b>) β (<b>b2</b>).</p>
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<p>SF statistics of columnar and equiaxed crystals.</p>
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<p>Columnar crystal phase distribution diagram (<b>a</b>). KAM part hcp crystal bcc crystal orientation diagram (<b>b</b>) and equiaxed crystal phase distribution diagram (<b>c</b>). KAM part hcp crystal bcc crystal orientation diagram (<b>d</b>).</p>
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32 pages, 11662 KiB  
Article
Molecular Docking and Experimental Analysis of Essential Oil-Based Preparations on Biofilm Formation on Orthodontic Archwires
by Vlad Tiberiu Alexa, Aurora Doris Fratila, Roxana Oancea, Atena Galuscan, Octavia Balean, Vanessa Bolchis, Berivan Laura Rebeca Buzatu, Diana Obistioiu, Mukhtar Adeiza Suleiman and Daniela Jumanca
Int. J. Mol. Sci. 2024, 25(24), 13378; https://doi.org/10.3390/ijms252413378 - 13 Dec 2024
Viewed by 390
Abstract
Good oral hygiene is crucial during treatment with fixed appliances, emphasising the need for additional or alternative oral health methods during orthodontic treatment. This study investigates the effect of essential oil (EO)-based preparations on biofilm adhesion to orthodontic archwires. Five identical-sized orthodontic archwires [...] Read more.
Good oral hygiene is crucial during treatment with fixed appliances, emphasising the need for additional or alternative oral health methods during orthodontic treatment. This study investigates the effect of essential oil (EO)-based preparations on biofilm adhesion to orthodontic archwires. Five identical-sized orthodontic archwires of different materials were tested using therapeutic and preventive applications of essential oils. This study also used molecular docking to explore how essential oil compounds interact with key proteins of common oral pathogens like Staphylococcus aureus and Streptococcus mutans. We found that the constituent materials heavily influence the antimicrobial effects of essential oils on different orthodontic archwires. Stainless steel-based orthodontic archwires demonstrated the highest efficacy in antimicrobial protection against S. mutans strains (maximum BIP = 28.82% on the epoxy-coated SS). Conversely, inhibition effects in preventive applications against S. aureus were observed exclusively with titanium–molybdenum alloy orthodontic archwires across all tested emulsions (maximum BIP = 29.44%). CuNiTi alloys showed ineffectiveness in preventive treatments, as none of the EO mixtures inhibited biofilm development on this material. After biofilm contamination with S. mutans and S. aureuss strains, the ternary emulsion was most effective for four out of five orthodontic archwires. Computational analysis revealed strong binding interactions between essential oil compounds and key proteins of S. aureus and S. mutans, highlighting specific amino acid residues that are critical for these interactions. Based on the results, stainless steel with epoxy coating or TMA archwires, combined with BEO/CEO/OEO ternary mixture, are recommended for optimal antibacterial protection against biofilm formation on orthodontic archwires. Full article
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Graphical abstract
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for preventive treatment against <span class="html-italic">S. mutans</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test; <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for preventive treatment against <span class="html-italic">S. mutans</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test; <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for preventive treatment against <span class="html-italic">S. mutans</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test; <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for preventive treatment against <span class="html-italic">S. aureus</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for preventive treatment against <span class="html-italic">S. aureus</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>BIP (%) values for preventive treatment against <span class="html-italic">S. mutans</span> (<b>a</b>) and <span class="html-italic">S. aureus</span> (<b>b</b>) and strains on different orthodontic archwires using natural preparation based on EOs.</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for curative treatment against <span class="html-italic">S. mutans</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for curative treatment against <span class="html-italic">S. mutans</span> strains on orthodontic archwires using natural preparation based on Eos. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for curative treatment against <span class="html-italic">S. aureus</span> strains on orthodontic archwires using natural preparation based on EOs. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for curative treatment against <span class="html-italic">S. aureus</span> strains on orthodontic archwires using natural preparation based on EOs. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>(<b>a</b>–<b>e</b>) BIP (%) values for curative treatment against <span class="html-italic">S. aureus</span> strains on orthodontic archwires using natural preparation based on EOs. (Different letters in columns indicate significant differences between values according to <span class="html-italic">t</span>-test, <span class="html-italic">p</span> &lt; 0.05. Superscript letters assigned to columns represent these differences).</p>
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<p>Optical microscopy image of <span class="html-italic">S. aureus</span> strains on orthodontic archwires (aesthetic epoxy coated stainless steel archwire) using natural preparation based on EOs (<b>a</b>) (without treatment), (<b>b</b>) (with BEO/CEO/OEO ternary mixture).</p>
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<p>Optical microscopy image of <span class="html-italic">S. mutans</span> strains on orthodontic archwires (aesthetic epoxy coated stainless steel archwire) treated with essential oil-based natural preparations (<b>a</b>) (without treatment), (<b>b</b>) (with BEO/CEO/OEO ternary mixture).</p>
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<p>Confocal images before (<b>a</b>) and after (<b>b</b>) treatment with natural preparation with BEO/CEO/OEO ternary mixture on aesthetic epoxy-coated stainless steel archwire.</p>
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<p>Three-dimensional surface plot of biofilm formation obtained with confocal microscope before (<b>a</b>) and after treatment (<b>b</b>) with natural preparation with BEO/CEO/OEO ternary mixture on the aesthetic epoxy-coated stainless steel archwire. <span class="html-italic">X</span>-axis represents horizontal spatial dimension of biofilm sample, in micrometres. <span class="html-italic">Y</span>-axis represents vertical spatial dimension perpendicular to t<span class="html-italic">X</span>-axis, in micrometres. <span class="html-italic">Z</span>-axis indicates height of microbial biofilm structure, corresponding to density and fluorescence signal intensity of biofilm. Green colouring highlights biofilm regions, and uneven surface suggests spatial variability in biofilm density.</p>
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<p>Best binding interaction between compounds (ligands) and 1ng5 protein (3D and 2D) as visualised in Discovery Studio.</p>
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<p>Best binding interaction between compound and 1T2P protein (3D and 2D) as visualised in Discovery Studio.</p>
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<p>Best binding interaction between compound and 3aie protein (3D and 2D) as visualised in Discovery Studio.</p>
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<p>Best binding interaction between compound and 3aie protein (3D and 2D) as visualised in Discovery Studio.</p>
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<p>Schematic workflow of the experimental strategy developed for the preventive and curative antimicrobial assays on orthodontic archwires using EOs. Figure created by the authors using Canva.com.</p>
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<p>Composition of natural preparations.</p>
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18 pages, 14264 KiB  
Article
An Investigation into the Ti-Nb-Ag Ternary System for Biocompatible Superelastic Alloys
by Ayush Prasad, Nicole L. Church and Nicholas G. Jones
Metals 2024, 14(12), 1426; https://doi.org/10.3390/met14121426 - 12 Dec 2024
Viewed by 522
Abstract
Superelastic metastable β-Ti-Nb alloys are attractive low-modulus materials for use in biomedical implants. The antibacterial properties of silver and its ability to lower the modulus of Ti-Nb-based transforming alloys make it an appealing ternary addition, but the Ti-Nb-Ag system is poorly characterised [...] Read more.
Superelastic metastable β-Ti-Nb alloys are attractive low-modulus materials for use in biomedical implants. The antibacterial properties of silver and its ability to lower the modulus of Ti-Nb-based transforming alloys make it an appealing ternary addition, but the Ti-Nb-Ag system is poorly characterised at present. This study elucidates the microstructure, equilibrium phases, and mechanical behaviour of a systematic series of Ti–24Nb–XAg (X = 0, 2, 6) (at.%) alloys. The mutual solubility of Nb and Ag in Ti overcame the immiscibility of Nb and Ag and produced an alloy with a single-phase β microstructure for low Ag concentrations. However, at silver concentrations above approximately 5 at.%, the solubility limit was reached and precipitates began to form. These precipitates were found to form quickly during recrystallisation, refining the grain size by Zener pinning, and persisted even after a 500 h heat treatment at 1100 °C. All three alloys showed non-linear-elastic behaviour typical of transforming alloys. The addition of up to 2 at.% Ag to Ti–24Nb was found to decrease the elastic modulus, suppress formation of the ω phase, and cause the critical transformation stress to decrease, though the transformation stress increased above that of Ti–24Nb when 6 at.% Ag is added. These results indicate that Ti-Nb-Ag alloys are a promising candidate for developing new low-modulus implants. Full article
(This article belongs to the Special Issue Advanced Biomedical Materials (2nd Edition))
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<p>SEM images for (<b>a</b>) Nb24, (<b>b</b>) Ag2, and (<b>c</b>) Ag6 in the as-cast condition. The inset in (<b>c</b>) shows the precipitates present in Ag6 at higher magnification.</p>
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<p>EDX maps of Ag6 in the as-cast condition.</p>
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<p>Laboratory XRD data for the alloys in the as-cast condition. The feature at ~ 25.7˚ 2<span class="html-italic">θ</span> indicated by * in each pattern was related to a collection artefact.</p>
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<p>SEM images of (<b>a</b>) Nb24, (<b>b</b>) Ag2, and (<b>c</b>) Ag6 in the RX condition. Note the different scale bar for (<b>c</b>).</p>
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<p>EDX maps for Nb24, Ag2, and Ag6 in the RX condition.</p>
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<p>XRD data for alloys in the RX condition. The markers at the top of the figure indicate reflections for the respective phases with relative intensities greater than 1% of that phase’s most intense peak. Note that peaks due to contamination by Cu K<sub><span class="html-italic">β</span></sub>, W L<sub><span class="html-italic">α</span>1</sub>, and W L<sub><span class="html-italic">α</span>2</sub> are present in the Ag2 data at 50.2°, 53.5°, and 54.0°, respectively.</p>
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<p>EDX maps for Ag2 and Ag6 after 500 h heat treatments.</p>
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<p>(<b>a</b>) XRD data for Ag2 after 500 h heat treatments; (<b>b</b>) XRD data for Ag6 after 500 h heat treatments.</p>
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<p>Uniaxial tensile data for Nb24, Ag2, and Ag6 in the RX condition. The dashed line shows a straight line through the origin in order to highlight the way in which the Ag6 tensile data curves away from linearity. Inset: Zoomed-in view of the initial linear elastic region.</p>
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<p>Full-ring synchrotron XRD data for Nb24, Ag2, and Ag6 after 5-minute recrystallisation. The features labelled with * are artefacts related to the EDM process.</p>
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36 pages, 10501 KiB  
Review
Advances in Corrosion of High-Temperature Materials: Interfacial Migration and Alloy Design Strategies
by Aditya Narayan Singh, Shashwat Kumar Swain, Abhishek Meena, Mobinul Islam and Kyung-Wan Nam
Ceramics 2024, 7(4), 1928-1963; https://doi.org/10.3390/ceramics7040121 (registering DOI) - 12 Dec 2024
Viewed by 757
Abstract
High-temperature structural materials face severe degradation challenges due to oxidation and corrosion, leading to reduced long-term stability and performance. This review comprehensively examines the interfacial migration mechanisms of reactive elements (REs) such as Ti, Al, and Cr in Ni/Fe-based alloys, emphasizing their role [...] Read more.
High-temperature structural materials face severe degradation challenges due to oxidation and corrosion, leading to reduced long-term stability and performance. This review comprehensively examines the interfacial migration mechanisms of reactive elements (REs) such as Ti, Al, and Cr in Ni/Fe-based alloys, emphasizing their role in forming and stabilizing protective oxide layers. We discuss how these oxide layers impede ion migration and mitigate environmental degradation. Key findings highlight the importance of selective oxidation, oxide layer healing, and the integration of novel alloying elements to enhance resistance under ultra-supercritical conditions. Advanced insights into grain boundary engineering, alloy design strategies, and quantum approaches to understanding charge transport at passive interfaces are also presented. These findings provide a foundation for developing next-generation high-temperature alloys with improved degradation resistance tailored to withstand extreme environmental conditions. Full article
(This article belongs to the Special Issue Advances in Ceramics, 2nd Edition)
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<p>A schematic representation of the corrosion phenomenon occurring inside a material exposed to environments.</p>
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<p>The schematic representation of oxide diffusing inside and metal cation diffusion outward. When metal atoms are ionized, they move into the oxide layer, creating a vacancy at the interface.</p>
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<p>(<b>a</b>) Microhardness profile for 316L-grade SS and various Mo composition in HEACs. (<b>b</b>) Obtained average friction coefficient. (<b>c</b>) Histogram plots showing the specific wear rates. Reproduced with permission from [<a href="#B74-ceramics-07-00121" class="html-bibr">74</a>], Elsevier, 2022. (<b>d</b>) The linear fit between YS and Al concentration for Al<sub>x</sub>(TiZrHfNb)<sub>100−x</sub>. (<b>e</b>) Profile showing wear rate and hardness variation with respect to Al concentration. (<b>f</b>) Logarithm plot of mass change against time (s) for Al-5/7/12 wt %. Reproduced with permission from [<a href="#B79-ceramics-07-00121" class="html-bibr">79</a>], Elsevier, 2022.</p>
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<p>(<b>a</b>) Water contact angle (WCA) and slip angle (SA) of SS and SHP-SS. (<b>b</b>) Polarization curve for SS (raw material) and SHP-SS (SS5; here, 5 indicates sample number with H<sub>2</sub>O<sub>2</sub>/HF ratio in 0.2/1, reaction time (50 min), and mass ratio of PFOS/HF in 1/100). (<b>c</b>) SEM image of SS5. Reproduced with permission from [<a href="#B95-ceramics-07-00121" class="html-bibr">95</a>], Elsevier, 2022. (<b>d</b>) Schematic illustration of DD5 superalloy with different crystallographic planes. (<b>e</b>) Potentiodynamic polarization curve in 3.5 wt % NaCl solution. (<b>f</b>) A potentiostatic polarization curve obtained in 3.5 wt % NaCl solution for DD5 superalloy with different planes. Reproduced with permission from [<a href="#B102-ceramics-07-00121" class="html-bibr">102</a>], Elsevier, 2022. (<b>g</b>) Various chemical energies for FCC Fe/Cr<sub>23</sub>C<sub>6</sub> interface with and without B-substitution of carbon atoms. Here, A1–A4 and B1–B3 signify the boron atom replacing carbon atoms in the first, second, third, and fourth layers of Cr<sub>23</sub>C<sub>6</sub> from A- and B-termination, respectively. (<b>h</b>) Side view of highly symmetrical (001) interface of FCC Fe/Cr<sub>23</sub>C<sub>6</sub>. Reproduced with permission from [<a href="#B104-ceramics-07-00121" class="html-bibr">104</a>], Elsevier, 2023.</p>
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<p>(<b>a</b>) Surface model for Ni (111): red—impurity atoms; blue—Ni; yellow—Ni site substituted by Cr atom (Case 1); green—Ni site substituted by Cr atom (Case 2). (<b>b</b>) Surface energies of Ni (111) and Ni-Cr systems, (1: Ni; 2: N/Ni; 3: O/Ni; 4: S/Ni; 5: P/Ni; 6: H/Ni; 7: Ni-Cr; 8: N/Ni-Cr; 9: O/Ni-Cr; 10: S/Ni-Cr; 11: P/Ni-Cr; 12: H/Ni-Cr). (<b>c</b>) Segregation energy of different impurity atoms onto Ni (111) and Ni-Cr (111) systems, (1: N/Ni; 2: N/Ni-Cr; 3: H/Ni; 4: H/Ni-Cr; 5: O/Ni; 6: O/Ni-Cr; 7: P/Ni; 8: P/Ni-Cr; 9: S/Ni; 10: S/Ni-Cr; 11: Cr/Ni). Reproduced with permission from [<a href="#B119-ceramics-07-00121" class="html-bibr">119</a>], Elsevier, 2019.</p>
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<p>(<b>a</b>) SEM images of the top surface. (<b>b</b>) Corresponding electron backscatter diffraction (EBSD) grain orientation map of sensitized as-received Al-Mg alloy after H<sub>3</sub>PO<sub>4</sub> etching. Black and yellow lines denote high-angle GBs (&gt;15°) and low-angle GBs (=15°), respectively. The white rectangle marks the special GBs of 13b. (<b>c</b>) Bar graph depicts the percentage length of as-received Al-Mg alloy in non-etched/etched GBs with H<sub>3</sub>PO<sub>4</sub> etching showing different misorientation angles. (<b>d</b>) Standard triangles denote the GB plane orientations of sensitized as-received Al-Mg alloy for fully-etched boundaries, (<b>e</b>) partially-etched boundaries, (<b>f</b>) non-etched boundaries, and (<b>g</b>) all boundaries. Reproduced from [<a href="#B125-ceramics-07-00121" class="html-bibr">125</a>], Springer Nature, 2016.</p>
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<p>Cross-sectional micrographs of sputtered Al-Mg alloy under FIB and TEM: (<b>a</b>) FIB cross-sectional image, and bright-field TEM (<b>b</b>) showing columnar grains. The inset image shows the selected area electron diffraction (SAED) pattern. (<b>c</b>) Cross-sectional image of transmitted backscatter electron diffraction sensitized sputtered Al-Mg alloy. The color of the grain corresponds to the plane orientation. Reproduced from [<a href="#B125-ceramics-07-00121" class="html-bibr">125</a>], Springer Nature, 2016.</p>
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<p>Effect of substituted Mg<sup>2+</sup> by novel cations on corrosion behavior. (<b>a</b>) The lattice parameters of α<sub>MgO</sub> and α<sub>Be-MgO</sub> are 4.293 and 4.201 Å, respectively. Their lattice values indicate a distorted structure on the accommodation of Be in the matrix. (<b>b</b>) The presence of Ce cation and its oxide together lies on and along the GBs and, ultimately, restricts the easy flow of Mg<sup>2+</sup> cations. Reproduced with permission from [<a href="#B168-ceramics-07-00121" class="html-bibr">168</a>], Elsevier, 2016. (<b>c</b>) the formation of MgO during oxidation at high temperatures increases the concentration of Nd on the surface, favoring the formation of a more stable passive layer of Nd<sub>2</sub>O<sub>3</sub>. Reproduced with permission from [<a href="#B175-ceramics-07-00121" class="html-bibr">175</a>], Elsevier, 2013.</p>
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<p>Corrosion morphologies after 3.5 wt % NaCl solution as revealed under optical microscope: (<b>a</b>) bare Ni-based alloy; and (<b>b</b>) Re-doped alloy. Scale bar is 400 μm. (<b>c</b>) Tafel plot of the alloys. (<b>d</b>,<b>e</b>) 3D morphologies of Re-doped alloy after high-temperature oxidation at 1000 °C for 10 h. Reproduced with permission from [<a href="#B190-ceramics-07-00121" class="html-bibr">190</a>], Elsevier, 2023.</p>
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22 pages, 5181 KiB  
Review
Laser Surface Texturing of Cutting Tools for Improving the Machining of Ti6Al4V: A Review
by Javier Garcia-Fernandez, Jorge Salguero, Moises Batista, Juan Manuel Vazquez-Martinez and Irene Del Sol
Metals 2024, 14(12), 1422; https://doi.org/10.3390/met14121422 - 12 Dec 2024
Viewed by 500
Abstract
The machining of titanium alloys, particularly Ti6Al4V, presents a significant challenge in manufacturing engineering. Its high strength, low thermal conductivity and high chemical reactivity make Ti6Al4V a hard-to-machine material. However, the machining process is critical for aerospace and biomedical industries. The rapid wear [...] Read more.
The machining of titanium alloys, particularly Ti6Al4V, presents a significant challenge in manufacturing engineering. Its high strength, low thermal conductivity and high chemical reactivity make Ti6Al4V a hard-to-machine material. However, the machining process is critical for aerospace and biomedical industries. The rapid wear and short lifetime of cutting tools are the main limitations in Ti6Al4V machining, leading to a large increase in manufacturing costs and compromising the surface quality of machined components. Faced with this problem, the texturing of cutting tools, especially through laser-based techniques, has gained considerable attention in the last decade due to improvement of the tribological properties of textured surfaces. Laser Surface Texturing (LST) has emerged as a promising technique to improve the tribological performance of cutting tools by enabling the creation of precise surface structures. Building on prior research, this review provides a comprehensive overview of the most recent research on this topic, summarizing key findings and outcomes from various investigations. Full article
(This article belongs to the Special Issue Advances in Metal Cutting and Machining Processes)
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<p>Scheme of types of texturing.</p>
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<p>Schematic configuration of LST by direct ablation.</p>
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<p>Ablation phenomena with different pulse durations: (<b>a</b>) short pulses and (<b>b</b>) ultrashort pulses. Adapted from Ref. [<a href="#B44-metals-14-01422" class="html-bibr">44</a>].</p>
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<p>Laser processing parameters for the development of surface textures.</p>
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<p>Microstructure morphology under different number of passes: (<b>a</b>) 1 pass, (<b>b</b>) 3 passes, (<b>c</b>) 5 passes and (<b>d</b>) 8 passes. Adapted from Ref. [<a href="#B57-metals-14-01422" class="html-bibr">57</a>].</p>
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<p>Dimples textures on the rake face. Adapted from Ref. [<a href="#B77-metals-14-01422" class="html-bibr">77</a>].</p>
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<p>Laser texturing of tungsten carbide substrate: (<b>a</b>) 16 J/cm<sup>2</sup>, 8 pulses; (<b>b</b>) 31 J/cm<sup>2</sup>, 8 pulses; (<b>c</b>) 47 J/cm<sup>2</sup>, 5 pulses; (<b>d</b>) 16 J/cm<sup>2</sup>, 5 pulses; (<b>e</b>) 31 J/cm<sup>2</sup>, 5 pulses; (<b>f</b>) 47 J/cm<sup>2</sup>, 5 pulses; (<b>g</b>) 16 J/cm<sup>2</sup>, 3 pulses; (<b>h</b>) 31 J/cm<sup>2</sup>, 3 pulses; and (<b>i</b>) 47 J/cm<sup>2</sup>, 3 pulses. Adapted from Ref. [<a href="#B79-metals-14-01422" class="html-bibr">79</a>].</p>
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<p>Graphical representation of orientation (<b>a</b>), geometry and shape (<b>b</b>), and density (<b>c</b>) parameters.</p>
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<p>Built-up edge (BUE) generated on a textured tool rake face. Adapted from Ref. [<a href="#B39-metals-14-01422" class="html-bibr">39</a>].</p>
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<p>Morphology of bionic microtexture. Adapted from Ref. [<a href="#B82-metals-14-01422" class="html-bibr">82</a>].</p>
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<p>Friction coefficient according to the friction path during the pin-on-disc test (before and after). Adapted from Ref. [<a href="#B88-metals-14-01422" class="html-bibr">88</a>].</p>
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22 pages, 3758 KiB  
Review
Laser Cladding In Situ Carbide-Reinforced Iron-Based Alloy Coating: A Review
by Junli Tang, Kaiming Wang and Hanguang Fu
Metals 2024, 14(12), 1419; https://doi.org/10.3390/met14121419 - 11 Dec 2024
Viewed by 491
Abstract
Laser cladding, as an advanced surface modification technology, has the advantages of a high energy density, controlled dilution rate and good metallurgical bonding between the coating and the substrate. Its rapid heating and cooling properties help to form a dense and fine coating [...] Read more.
Laser cladding, as an advanced surface modification technology, has the advantages of a high energy density, controlled dilution rate and good metallurgical bonding between the coating and the substrate. Its rapid heating and cooling properties help to form a dense and fine coating structure on the surface of the substrate, thus enhancing wear and corrosion resistance. In recent years, the in situ generation of carbide-reinforced iron-based composite coatings has gradually become a research hotspot because it combines the high hardness values of carbide with the high toughness values of iron-based alloys, which significantly improves the comprehensive performance of the coatings. This paper reviews the research progress of laser cladding in situ carbide-reinforced iron-based alloy coatings and explores the role of different types of in situ synthesized carbides (TiC, NbC, WC, etc.) in the coatings and their effects on their wear resistance and mechanical properties. The distribution of carbides in the coatings and their morphological characteristics are also discussed, and the effects of laser power, scanning speed and auxiliary treatments (ultrasonic vibration, induction heating, etc.) on the microstructure and properties of the coatings are analyzed. Finally, the problems and future directions of development in this field are envisioned. Full article
(This article belongs to the Special Issue Laser Additive Manufacturing of Alloys)
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<p>Laser cladding process. (<b>a</b>) Components of the laser cladding system; (<b>b</b>) Melt pool reaction. Reprinted from Ref. [<a href="#B10-metals-14-01419" class="html-bibr">10</a>].</p>
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<p>The effect of varying nano-WC contents on the wear rate of Fe-based coatings. Reprinted from Ref. [<a href="#B13-metals-14-01419" class="html-bibr">13</a>].</p>
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<p>SEM cross-sectional images of in situ synthesized 316L stainless steel reinforced with different TiC contents: (<b>a</b>) 3.6% TiC; (<b>b</b>) 3.6% TiC; (<b>c</b>) 3.6% TiC. Reprinted with permission from Ref. [<a href="#B18-metals-14-01419" class="html-bibr">18</a>]. Copyright 2024 Elsevier.</p>
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<p>Mechanism of in situ synthesized WC in iron-based alloys: (<b>a</b>) above 1340 °C; (<b>b</b>) 1340 °C; (<b>c</b>) 1190 °C; (<b>d</b>) 640 °C; (<b>e</b>) 600 °C; (<b>f</b>) 450 °C. Reprinted with permission from Ref. [<a href="#B22-metals-14-01419" class="html-bibr">22</a>]. Copyright 2024 TRIBOLOGY.</p>
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<p>Phase evolution process of in situ synthesized NbC: (<b>a</b>) Phase distribution of the Fe-based coating, (<b>b</b>) Phase distribution of the composite coating. Reprinted with permission from Ref. [<a href="#B26-metals-14-01419" class="html-bibr">26</a>]. Copyright 2024 Elsevier.</p>
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<p>Variation in microhardness of coatings along the depth direction at different CeO<sub>2</sub> contents. Reprinted with permission from Ref. [<a href="#B40-metals-14-01419" class="html-bibr">40</a>]. Copyright 2024 Elsevier.</p>
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<p>Effect of process parameters on clad height (<b>H</b>): (<b>a</b>) variation in H with shielding gas flow rate (G) at different scanning speeds (v); (<b>b</b>) variation in H with v at different laser power values (P); (<b>c</b>) variation in H with P at different G values. Reprinted with permission from Ref. [<a href="#B41-metals-14-01419" class="html-bibr">41</a>]. Copyright 2024 Elsevier.</p>
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<p>Pareto front solution set under different process parameters. Reprinted with permission from Ref. [<a href="#B45-metals-14-01419" class="html-bibr">45</a>]. Copyright 2024 Elsevier.</p>
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<p>Size and distribution of enhanced phases of coatings at different ultrasonic vibration powers: (<b>a</b>) 0 W; (<b>b</b>) 100 W; (<b>c</b>) 200 W; (<b>d</b>) 300 W. Reprinted with permission from Ref. [<a href="#B53-metals-14-01419" class="html-bibr">53</a>]. Copyright 2024 Elsevier.</p>
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<p>Thermal imaging photograph of the molten pool taken by an infrared camera. (<b>a</b>) Using an induction heater; (<b>b</b>) Without using an induction heater. Reprinted with permission from Ref. [<a href="#B57-metals-14-01419" class="html-bibr">57</a>]. Copyright 2024 Elsevier.</p>
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19 pages, 6647 KiB  
Article
The Design and Application of an Advanced System for the Diagnosis and Treatment of Flatfoot Based on Infrared Thermography and a Smart-Memory-Alloy-Reinforced Insole
by Ali F. Abdulkareem, Auns Q. Al-Neami, Tariq J. Mohammed and Hayder R. Al-Omairi
Prosthesis 2024, 6(6), 1491-1509; https://doi.org/10.3390/prosthesis6060108 - 9 Dec 2024
Viewed by 477
Abstract
Background: Flatfoot deformity is a common condition in children and teenagers that may increase the risk of knee, hip, and back pain. Most of the insoles suggested to treat flatfoot symptoms are not designed to adapt to foot temperature during walking, and they [...] Read more.
Background: Flatfoot deformity is a common condition in children and teenagers that may increase the risk of knee, hip, and back pain. Most of the insoles suggested to treat flatfoot symptoms are not designed to adapt to foot temperature during walking, and they are either too soft to provide support or hard enough to be uncomfortable. Purpose: This study aims to develop an advanced solution to diagnose and treat flexible flatfoot (FFT) using infrared thermography measurements and a hybrid insole reinforced by nitinol (NiTiCu) smart-memory-alloy wires (SMAWs), this super-elastic alloy can return back to its pre-deformed shape when heated, which helps to reduce the local high-temperature points caused by the uneven pressure of FFT. This approach achieves a more uniform thermal distribution across the foot, which makes the hybrid insole more comfortable. Methods: The study involved 16 subjects, divided into two groups of eight flat-footed and eight normal. The procedure includes two parts, namely, designing a prototype insole with SMAW properties based on thermography measurement by using SolidWorks, and evaluating this design using Ansys. Second, a hybrid insole reinforced with SMAWs is customized for flatfoot subjects. The thermography measurement differences between the medial and lateral sides of the metatarsophalangeal line are compared for the normal and flatfoot groups before and after wearing the suggested design. Results: The results show that our approach safely diagnosed FFT and significantly improved the thermal distribution in FFT subjects by more than 80% after wearing the suggested design. A paired t-test reported significant (p-value > 0.001) thermal decreases in the high-temperature points after using the SMAW insole, which was closely approximated to the normal subjects. Conclusions: the SMAW-reinforced insole is comfortable and suitable for treating FFT deformity, and infrared thermography is an effective tool to evaluate FFT deformity. Full article
(This article belongs to the Special Issue Recent Advances in Foot Prosthesis and Orthosis)
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<p>Experimental procedure and study design.</p>
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<p>SolidWorks insole trace.</p>
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<p>SolidWorks template design.</p>
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<p>CNC-carved graphite template with NiTiCu wires fixed inside it, so that it can reshape and take the medial arch foot shape.</p>
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<p>Reshaped NiTiCu SMA wires.</p>
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<p>Manufactured insole reinforced by NiTiCu SMA wires.</p>
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<p>The subjects’ results of the temperature differences between the medial and lateral lines. (A) The blue bar represents the flatfoot group before wearing the NiTiCu insole; (B) the red bar represents the flatfoot group after wearing the hybrid insole; and (C) the green bar represents the normal subjects. Three stars (***) indicate a significance level of <span class="html-italic">p</span>-value &lt; 0.001, which was reported by comparing the flatfoot group before and after wearing the NiTiCu insole, and <span class="html-italic">p</span>-value &lt; 0.001 when comparing the flatfoot group without the NiTiCu insole with normal subjects.</p>
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<p>The thermal distribution of a (<b>A</b>) FFT subject before wearing the NiTiCu insole, the average temperature difference between the medial and lateral sides is 1.25 °C; (<b>B</b>) the same flatfoot subject after wearing the NiTiCu insole, the temperature difference between the medial and lateral sides is 0.09 °C; and (<b>C</b>) the temperature difference of a normal subject between the medial and lateral sides is 0.06 °C.</p>
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<p>(<b>A</b>) Side and (<b>B</b>) top view of the imaginary insole.</p>
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<p>(<b>a</b>,<b>b</b>) show the total upward vertical deformation using Ansys software (max: 1.3078 mm).</p>
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<p>Equivalent upward vertical Von-mises stress (max: 16.383 MPa).</p>
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<p>Equivalent downward vertical Von-mises stress (max: 0.016646 MPa).</p>
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<p>Total downward vertical deformation (max: −0.061132 mm).</p>
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