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Search Results (21,813)

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Keywords = steel

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26 pages, 663 KiB  
Article
Effect of Preload on Box-Section Steel Columns Filled with Concrete under Axial Load: A Numerical Study
by Ahmed Mohamed Sayed
Buildings 2024, 14(9), 2924; https://doi.org/10.3390/buildings14092924 (registering DOI) - 15 Sep 2024
Abstract
External loads applied to a box-section steel column before it is filled with concrete to increase its efficiency due to modifications in structural systems or design errors may reduce its ultimate capacity and change its structural behavior. To examine this effect, finite element [...] Read more.
External loads applied to a box-section steel column before it is filled with concrete to increase its efficiency due to modifications in structural systems or design errors may reduce its ultimate capacity and change its structural behavior. To examine this effect, finite element modeling (FEM) has been used to simulate these columns under preloading at different ratios with many variables in the geometric dimensions of the columns. The FEM results have been investigated using 38 experimental specimens obtained from previous studies without preloading. The results demonstrated high accuracy in modeling these columns in structural behavior and ultimate load capacity. After verifying the results, 84 Concrete-Filled Steel Columns (CFSC) were modeled under different preload ratios. The results indicated that some variables have directly affected the value of the decrease in column capacity in terms of its height, wall thickness, yield stress, and preload ratios, while others were inversely proportional in terms of the cross-section dimensions and concrete strength. The preload effect ratio had two separate limits, where when it reached 70%, the maximum value of the decrease in column capacity was 10.90%. The value increased sharply reaching 19.90% when there was a preload equal to 80%. New equations have been proposed to predict the ultimate capacity of CFSC under preloading with suitable accuracy with a correlation coefficient of no less than 0.949. Full article
(This article belongs to the Special Issue Advances in Steel–Concrete Composite Structures)
17 pages, 6295 KiB  
Article
Study on the Effect of Pressure on the Microstructure, Mechanical Properties, and Impact Wear Behavior of Mn-Cr-Ni-Mo Alloyed Steel Fabricated by Squeeze Casting
by Bo Qiu, Longxia Jia, Heng Yang, Zhuoyu Guo, Chuyun Jiang, Shuting Li and Biao Sun
Metals 2024, 14(9), 1054; https://doi.org/10.3390/met14091054 (registering DOI) - 15 Sep 2024
Abstract
ZG25MnCrNiMo steel samples were prepared by squeeze casting under pressure ranging from 0 to 150 MPa. The effects of pressure on the microstructure, low-temperature toughness, hardness, and impact wear performance of the prepared steels were experimentally investigated. The experimental results indicated that the [...] Read more.
ZG25MnCrNiMo steel samples were prepared by squeeze casting under pressure ranging from 0 to 150 MPa. The effects of pressure on the microstructure, low-temperature toughness, hardness, and impact wear performance of the prepared steels were experimentally investigated. The experimental results indicated that the samples fabricated under pressure exhibited finer grains and a significant ferrite content compared to those produced without pressure. Furthermore, the secondary dendrite arm spacing of the sample produced at 150 MPa decreased by 45.3%, and the ferrite content increased by 39.1% in comparison to the unpressurized sample. The low-temperature impact toughness of the steel at −40 °C initially increased and then decreased as the pressure varied from 0 MPa to 150 MPa. And the toughness achieved an optimal value at a pressure of 30 MPa, which was 65.4% greater than that of gravity casting (0 MPa), while the hardness decreased by only 6.17%. With a further increase in pressure, the impact work decreased linearly while the hardness increased slightly. Impact fracture analysis revealed that the fracture of the steel produced without pressure exhibited a quasi-cleavage morphology. The samples prepared by squeeze casting under 30 MPa still exhibited a large number of fine dimples even at −40 °C, indicative of ductile fracture. In addition, the impact wear performance of the steels displayed a trend of initially decreasing and subsequently increasing across the pressure range of 0–150 MPa. The wear resistance of samples prepared without pressure and at 30 MPa was superior to that at 60 MPa, and the wear resistance deteriorated when the pressure increased to 60 MPa, after which it exhibited an upward trend as the pressure continued to rise. The wear mechanisms of the samples predominantly consisted of impact wear, adhesive wear, and minimal abrasive wear, along with notable occurrences of plastic removal, furrows, and spalling. Full article
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Figure 1
<p>Sampling position diagram of the prepared sample.</p>
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<p>Microstructure of the samples prepared under different pressures: (<b>a</b>) 0 MPa; (<b>b</b>) 30 MPa; (<b>c</b>) 60 MPa; (<b>d</b>) 90 MPa; (<b>e</b>) 120 MPa; (<b>f</b>) 150 MPa.</p>
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<p>Secondary dendrite arm spacing and ferritic content of the samples prepared under different pressures.</p>
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<p>SEM images at a higher magnification of the microstructure of the samples prepared under different pressures: (<b>a</b>) 0 MPa; (<b>b</b>) 30 MPa; (<b>c</b>) 60 MPa; (<b>d</b>) 90 MPa; (<b>e</b>) 120 MPa; (<b>f</b>) 150 MPa.</p>
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<p>XRD analysis of the steel prepared under various pressures.</p>
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<p>Variation in the density and porosity of the steels prepared at different pressures.</p>
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<p>(<b>a</b>) Brinell hardness of the samples prepared under different pressures; (<b>b</b>) low-temperature (−40 °C) impact energy of the samples prepared under different pressures.</p>
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<p>Macro- and micro-impact fracture morphology of the samples prepared under different pressures: (<b>a</b>–<b>a’</b>) 0 MPa; (<b>b</b>–<b>b’</b>) 30 MPa; (<b>c</b>–<b>c’</b>) 60 MPa; (<b>d</b>–<b>d’</b>) 90 MPa; (<b>e</b>–<b>e’</b>) 120 MPa; (<b>f</b>–<b>f’</b>) 150 MPa.</p>
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<p>EDS analysis results of the impact fracture morphology for the sample prepared under 30 MPa: (<b>a</b>) site 1; (<b>b</b>) site 2.</p>
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<p>(<b>a</b>) Relationship between wear time and wear loss of the samples prepared under different pressures; (<b>b</b>) wear rate of the samples prepared under different pressures.</p>
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<p>Morphology of the worn surface of the samples prepared under different pressures: (<b>a</b>) 0 MPa; (<b>b</b>) 30 MPa; (<b>c</b>) 60 MPa; (<b>d</b>) 90 MPa; (<b>e</b>) 120 MPa; (<b>f</b>) 150 MPa.</p>
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17 pages, 3315 KiB  
Article
Application of the Gradient-Boosting with Regression Trees to Predict the Coefficient of Friction on Drawbead in Sheet Metal Forming
by Sherwan Mohammed Najm, Tomasz Trzepieciński, Salah Eddine Laouini, Marek Kowalik, Romuald Fejkiel and Rafał Kowalik
Materials 2024, 17(18), 4540; https://doi.org/10.3390/ma17184540 (registering DOI) - 15 Sep 2024
Abstract
Correct design of the sheet metal forming process requires knowledge of the friction phenomenon occurring in various areas of the drawpiece. Additionally, the friction at the drawbead is decisive to ensure that the sheet flows in the desired direction. This article presents the [...] Read more.
Correct design of the sheet metal forming process requires knowledge of the friction phenomenon occurring in various areas of the drawpiece. Additionally, the friction at the drawbead is decisive to ensure that the sheet flows in the desired direction. This article presents the results of experimental tests enabling the determination of the coefficient of friction at the drawbead and using a specially designed tribometer. The test material was a DC04 carbon steel sheet. The tests were carried out for different orientations of the samples in relation to the sheet rolling direction, different drawbead heights, different lubrication conditions and different average roughnesses of the countersamples. According to the aim of this work, the Features Importance analysis, conducted using the Gradient-Boosted Regression Trees algorithm, was used to find the influence of several parameter features on the coefficient of friction. The advantage of gradient-boosted decision trees is their ability to analyze complex relationships in the data and protect against overfitting. Another advantage is that there is no need for prior data processing. According to the best of the authors’ knowledge, the effectiveness of gradient-boosted decision trees in analyzing the friction occurring in the drawbead in sheet metal forming has not been previously studied. To improve the accuracy of the model, five MinLeafs were applied to the regression tree, together with 500 ensembles utilized for learning the previously learned nodes, noting that the MinLeaf indicates the minimum number of leaf node observations. The least-squares-boosting technique, often known as LSBoost, is used to train a group of regression trees. Features Importance analysis has shown that the friction conditions (dry friction of lubricated conditions) had the most significant influence on the coefficient of friction, at 56.98%, followed by the drawbead height, at 23.41%, and the sample width, at 11.95%. The average surface roughness of rollers and sample orientation have the smallest impact on the value of the coefficient of friction at 6.09% and 1.57%, respectively. The dispersion and deviation observed for the testing dataset from the experimental data indicate the model’s ability to predict the values of the coefficient of friction at a coefficient of determination of R2 = 0.972 and a mean-squared error of MSE = 0.000048. It was qualitatively found that in order to ensure the optimal (the lowest) coefficient of friction, it is necessary to control the friction conditions (use of lubricant) and the drawbead height. Full article
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Figure 1
<p>3D surface topography and selected roughness parameters of DC04 steel sheet.</p>
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<p>(<b>a</b>) Diagram and (<b>b</b>) view of the testing device: 1, 2, 3—working rollers; 4—support roller; 5—body; 6—sample; 7—nut; 8—horizontal tension cell; 9—upper tension cell; 10, 11—load cells.</p>
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<p>Scheme of force parameters for the test carried out with (<b>a</b>) fixed and (<b>b</b>) freely rotating rollers.</p>
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<p>Model performance of the training and testing iterations.</p>
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<p>SHAP value plot influence on COF.</p>
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<p>Relative importance of input parameters on COF; (<b>a</b>) ordered bar chart and (<b>b</b>) pie chart with percentage.</p>
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<p>Actual and predicted values; (<b>a</b>) training COF dataset and (<b>b</b>) testing COF dataset.</p>
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<p>Actual and predicted values of training COF dataset with 0.1 adjusting.</p>
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<p>Actual and predicted values of COF; (<b>a</b>) training dataset and (<b>b</b>) testing dataset.</p>
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19 pages, 9105 KiB  
Article
Inhibiting Eutectic Si Macrosegregation in Squeeze Cast A356 Alloy by Symmetrical Multidirectional Pressure
by Weitao Cai, Xiaozu Zhang, Dongtao Wang, Wenping Weng, Zibin Wu and Hiromi Nagaumi
Symmetry 2024, 16(9), 1213; https://doi.org/10.3390/sym16091213 (registering DOI) - 15 Sep 2024
Abstract
The process of symmetrical multidirectional pressure was adopted to inhibit the macrosegregation of eutectic Si in squeeze cast A356 alloy. Five pressure modes were applied to study the effects of multidirectional pressure and the timing of pressure application on the macrosegregation of eutectic [...] Read more.
The process of symmetrical multidirectional pressure was adopted to inhibit the macrosegregation of eutectic Si in squeeze cast A356 alloy. Five pressure modes were applied to study the effects of multidirectional pressure and the timing of pressure application on the macrosegregation of eutectic Si. The results show that the directional movement of the solute-rich liquid phase could be inhibited by symmetrical multidirectional pressure. Therefore, the macrosegregation of eutectic Si in the casting part was inhibited. Moreover, the timing of pressure application should be matched with the local pressure position. After the effective inhibition of the macrosegregation of eutectic Si, the elongation of the alloy was significantly improved, reaching up to 7.12%. In addition, the plastic deformation region was observed at the local pressure position. The grains in the plastic deformation region were refined. The proportion of low-angle grain boundaries in the deformed region was about 30%, which was much higher than that in the other undeformed region. The size of the Fe-containing intermetallics in the deformed region decreased to 5–10 μm, which is favorable for the mechanical properties of the alloy. Full article
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Figure 1
<p>(<b>a</b>) The schematic diagram of the multidirectional squeeze casting mold; (<b>b</b>) the step number of the multidirectional squeeze casting; (<b>c</b>) the sampling position diagram of each step (α is the local pressurization position of the narrow side, β is the local pressurization position of the wide side, 1/2/3 are sampled from the edge to the center of the ingot, <span class="html-italic">F<sub>s</sub></span> is the local pressure in the four directions of the horizontal plane, and <span class="html-italic">F<sub>D</sub></span> is the master cylinder pressure).</p>
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<p>Schematic of tensile test samples in this paper (unit: mm): (<b>a</b>) sampling location; (<b>b</b>) schematic and dimensions of tensile test samples.</p>
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<p>Macrostructures of β-3 at the ξ1 and ξ4 steps under the conditions of unidirectional pressure (A1, A2) and multidirectional pressure (A3). The ξ1 step of the squeeze casting: (<b>a</b>) the schematic diagram; (<b>b</b>) A1; (<b>c</b>) A2; (<b>d</b>) A3. The ξ4 step of the squeeze casting: (<b>e</b>) the schematic diagram; (<b>f</b>) A1; (<b>g</b>) A2; (<b>h</b>) A3.</p>
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<p>Microstructures of the samples solidified with A2 conditions. The ξ1 step of the casting: (<b>a</b>) β-1, (<b>b</b>) β-2, (<b>c</b>) β-3; the ξ2 step of the casting: (<b>d</b>) β-1, (<b>e</b>) β-2, (<b>f</b>) β-3; the ξ3 step of the casting: (<b>g</b>) β-1, (<b>h</b>) β-2, (<b>i</b>) β-3; the ξ4 step of the casting: (<b>j</b>) β-1, (<b>k</b>) β-2, (<b>l</b>) β-3.</p>
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<p>(<b>a</b>) SEM diagram of the macrosegregation region shown in the arrow of <a href="#symmetry-16-01213-f004" class="html-fig">Figure 4</a>c. (<b>b</b>) is the distribution of Al element, (<b>c</b>) is the distribution of Si element, and (<b>d</b>) is the distribution of Mg element.</p>
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<p>Microstructures of A2-ξ4 alloy. (<b>a</b>,<b>d</b>): β-1; (<b>b</b>,<b>e</b>): β-2; (<b>c</b>,<b>f</b>): β-3.</p>
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<p>Comparison of microstructures at the ξ1 step: A1-ξ1: (<b>a</b>) β-1, (<b>b</b>) β-2, (<b>c</b>) β-3; A2-ξ1: (<b>d</b>) β-1, (<b>e</b>) β-2, (<b>f</b>) β-3.</p>
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<p>The schematic diagram of the pressure mode and microstructures of the alloys solidified under A3 conditions. (<b>a</b>) schematic diagram of pressure mode, (<b>b</b>) and (<b>c</b>): ξ1-β-3; (<b>d</b>) and (<b>e</b>): ξ2-β-3; (<b>f</b>) and (<b>g</b>): ξ3-β-3; (<b>h</b>) and (<b>i</b>): ξ4-β-3.</p>
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<p>Simulation curve of non-equilibrium solidification.</p>
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<p>The schematic diagram of applying pressure and microstructures of ξ1–ξ4 alloys under A4 and A5 conditions. (<b>a</b>) schematic diagram of applying pressure; A4 conditions: (<b>b</b>) ξ1-β-3, (<b>d</b>) ξ2-β-3, (<b>f</b>) ξ3-β-3, (<b>h</b>) ξ4-β-3; A5 conditions: (<b>c</b>) ξ1-β-3, (<b>e</b>) ξ2-β-3, (<b>g</b>) ξ3-β-3, (<b>i</b>) ξ4-β-3.</p>
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<p>Engineering stress–strain curves of alloys with different pressure modes.</p>
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<p>The tensile fracture morphologies of the alloys under different conditions. (<b>a</b>) A2, (<b>b</b>) A5.</p>
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<p>Plastic deformation microstructures of β-(1/2) alloys under the conditions of A3 and A5. (<b>a</b>) A3-ξ2-β-1, (<b>b</b>) A3-ξ2-β-1, (<b>c</b>) A3-ξ2-β-2, (<b>d</b>) A5-ξ3-β-1, (<b>e</b>) A5-ξ3-β-1, (<b>f</b>) A5-ξ3-β-2.</p>
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<p>Images of EBSD of α-1 position samples solidified with A3, A4 and A5 pressure modes: (<b>a</b>) A3-ξ3; (<b>b</b>) A4-ξ2; (<b>c</b>) A5-ξ2; (<b>d</b>) A3-ξ2; (<b>e</b>) A4-ξ3; (<b>f</b>) A5-ξ3.</p>
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<p>EBSD results of plastic deformation region of A3-ξ2-α-1 alloy: (<b>a</b>) grain structure; (<b>b</b>) low-angle/high-angle grain boundaries distribution of grain structure (the low-angle grain boundaries (2° &lt; θ &lt; 15°) are marked with red lines, and the high-angle grain boundaries (θ &gt; 15°) are marked with black lines); (<b>c</b>) statistics of low-angle and high-angle grain boundaries; (<b>d</b>) KAM (kernel average misorientation) image (the green region represents the dislocation pile-up region).</p>
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<p>EBSD results of plastic deformation region of A4-ξ3-α-1 alloy: (<b>a</b>) grain structure; (<b>b</b>) low-angle/high-angle grain boundaries distribution of grain structure (the low-angle grain boundaries (2° &lt; θ &lt; 15°) are marked with red lines, and the high-angle grain boundaries (θ &gt; 15°) are marked with black lines); (<b>c</b>) statistics of low-angle and high-angle grain boundaries; (<b>d</b>) KAM image (the green region represents the dislocation pile-up region).</p>
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<p>EBSD results of plastic deformation region of A5-ξ3-α-1 alloy: (<b>a</b>) grain structure; (<b>b</b>) low-angle/high-angle grain boundaries distribution of grain structure (the low-angle grain boundaries (2° &lt; θ &lt; 15°) are marked with red lines, and the high-angle grain boundaries (θ &gt; 15°) are marked with black lines); (<b>c</b>) statistics of low-angle and high-angle grain boundaries; (<b>d</b>) KAM image (the green region represents the dislocation pile-up region).</p>
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<p>SEM analysis of Fe-containing intermetallics in the plastic deformation region: (<b>a</b>,<b>b</b>) A3-ξ2-α-1 alloy; (<b>e</b>,<b>f</b>) A5-ξ3-α-1 alloy. (<b>c</b>,<b>d</b>,<b>g,h</b>) are the components of phase (1), (2), (3) and (4), respectively.</p>
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15 pages, 7399 KiB  
Article
Analysis of the Wear Parameters and Microstructure of High-Carbon Steel in Order to Identify Its Tribological Properties
by Janusz Krawczyk, Łukasz Frocisz, Piotr Matusiewicz, Mateusz Kopyściański and Sebastian Lech
Appl. Sci. 2024, 14(18), 8318; https://doi.org/10.3390/app14188318 (registering DOI) - 15 Sep 2024
Abstract
Alloyed high-carbon steels are materials primarily intended for components operating under conditions of intense tribological wear. The carbides present in the microstructure of these materials significantly contribute to improving the wear resistance of such alloys. However, changes in the morphology of these precipitates [...] Read more.
Alloyed high-carbon steels are materials primarily intended for components operating under conditions of intense tribological wear. The carbides present in the microstructure of these materials significantly contribute to improving the wear resistance of such alloys. However, changes in the morphology of these precipitates can considerably alter the wear rate, leading to a deterioration in the properties of the materials. Therefore, this study aims to analyze the influence of several factors on the tribological wear of alloyed high-carbon steel. The research included friction tests under various load conditions and different sliding paths. Additionally, the samples were subjected to heat treatment to change the morphology of the observed precipitates. The tribological tests were conducted in a block-on-ring configuration under dry friction conditions. The tribological tests were analyzed statistically using analysis of variance (ANOVA). The results of the statistical analysis indicated that the primary factor influencing the observed differences between the samples was the heat treatment time of the material. Additionally, there were no significant statistical differences when pressure and friction path were varied. These findings, in conjunction with the SEM studies, allowed for the evaluation of the wear mechanism. The results demonstrated that, within the adopted tribological system, no alterations in the wear mechanism were observed with changes in test parameters. The observed differences in wear properties between the samples were found to be related to their heat treatment. The heat treatment resulted in alterations to the particle size distribution, with the annealing of the material at an elevated temperature leading to the dissolution of finer particles within the material. An increase in the average diameter of the carbide present in the material was observed to improve the wear resistance of the alloy tested. Full article
(This article belongs to the Section Materials Science and Engineering)
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Figure 1
<p>The dilatometric curve for the investigated material.</p>
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<p>Examples of friction coefficient change curves during the test. Variant 100 N-2000 s; (<b>a</b>) 4 h, (<b>b</b>) 8 h, and (<b>c</b>) 12 h.</p>
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<p>Results of the tribological test, (<b>a</b>) mass loss of the samples in correlation to the time of material annealing, (<b>b</b>) average friction coefficient in relation to annealing time, (<b>c</b>) wear depth in relation to the annealing time, and (<b>d</b>) wear depth in relation to force used during the test.</p>
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<p>Surface of samples after tribological testing, area of abrasion, (<b>a</b>)—4 h-100 N-2000 s; (<b>b</b>)—4 h-100 N-4000 s; (<b>c</b>) 4 h-150 N-2000 s; (<b>d</b>) 8 h-100 N-2000 s; (<b>e</b>)—8 h-100 N-4000 s; (<b>f</b>)—8 h-150 N-2000 s; (<b>g</b>)—12 h-100 N-2000 s; (<b>h</b>)—12 h-100 N-4000 s; (<b>i</b>)—12 h-150 N-2000 s.</p>
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<p>Microstructure of the investigated material: (<b>a</b>,<b>d</b>)—4 h annealing; (<b>b</b>,<b>e</b>)—8 h annealing; (<b>c</b>,<b>f</b>)—12 h annealing.</p>
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<p>Frequency distribution of carbide sizes for the test samples. (<b>a</b>) 4 h of annealing, (<b>b</b>) 8 h of annealing, (<b>c</b>) 12 h of annealing.</p>
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<p>Dependence of the average hardness of the tested samples on the annealing time.</p>
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19 pages, 1375 KiB  
Review
Aluminum Conductor Steel-Supported Conductors for the Sustainable Growth of Power Line Capacity: A Review and Discussion
by Milad Jalilian, Jordi-Roger Riba and Pooya Parvizi
Materials 2024, 17(18), 4536; https://doi.org/10.3390/ma17184536 (registering DOI) - 15 Sep 2024
Viewed by 190
Abstract
Industrial development and population growth have increased the need for higher-capacity power transmission lines. Aluminum conductor steel-supported (ACSS) conductors, a type of high-temperature low-sag (HTLS) conductor, are now widely used in new designs and reconductoring applications. ACSS conductors are preferred over traditional aluminum [...] Read more.
Industrial development and population growth have increased the need for higher-capacity power transmission lines. Aluminum conductor steel-supported (ACSS) conductors, a type of high-temperature low-sag (HTLS) conductor, are now widely used in new designs and reconductoring applications. ACSS conductors are preferred over traditional aluminum conductor steel-reinforced (ACSR) conductors due to their high strength, low sag, and excellent thermal stability. These attributes have garnered significant interest from researchers, engineers, and manufacturers. This paper provides a comprehensive review of the structure, properties, testing methods, and environmental behavior of ACSS conductors. Full article
(This article belongs to the Section Energy Materials)
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<p>The production process of aluminum-clad steel wires (AW).</p>
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<p>The production process of galvanized steel wires (GA).</p>
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<p>(<b>a</b>) Production diagram of an ACSS conductor and (<b>b</b>) schematic of an ACSS conductor.</p>
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14 pages, 6981 KiB  
Article
Corrosion Behaviour of Weld Metal of Ultra-High-Strength Steel Weldments in a Sodium Chloride Aqueous Solution
by Mariana Ilieva, Danail Gospodinov, Nikolay Ferdinandov and Rossen Radev
Materials 2024, 17(18), 4534; https://doi.org/10.3390/ma17184534 (registering DOI) - 15 Sep 2024
Viewed by 188
Abstract
As high-strength and ultra-high-strength steels are widely used in all kinds of modern welded constructions, a lot of research is carried out to investigate the mechanical properties of the weldments of these steels, but there is little information on such important characteristics as [...] Read more.
As high-strength and ultra-high-strength steels are widely used in all kinds of modern welded constructions, a lot of research is carried out to investigate the mechanical properties of the weldments of these steels, but there is little information on such important characteristics as their corrosion behaviour. This research focuses on the corrosion behaviour of the weld metal of the weldments of S906QL and S700MC steels. The weld metal was tested electrochemically in a 3.5% NaCl aqueous solution via a potentiodynamic scan to determine the corrosion rate and its dependence on the welding gap. No influence of the welding gap on the corrosion rate was found, but the experimental results suggested that the corrosion rate depended on the chemical composition of the filler material and the microstructure of the weld metal. Full article
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<p>Macrostructure of the weldments, longitudinal section.</p>
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<p>Macrostructure of weldments of S960QL, cross-section.</p>
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<p>Macrostructure of weldments of S700MC, cross-section.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S960QL at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S960QL at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S700MC at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S700MC at two different magnifications.</p>
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<p>Open circuit potential of S960QL and weld metal of weldments of S960QL in a 3.5% NaCl water solution at room temperature.</p>
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<p>Open circuit potential of S700MC and weld metal of weldments of S700MC in a 3.5% NaCl water solution at room temperature.</p>
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<p>Polarisation curves of S960QL and weld metal of weldments of S960QL in a 3.5% NaCl water solution at room temperature.</p>
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<p>Polarisation curves of S700MC and weld metal of weldments of S700MC in a 3.5% NaCl water solution at room temperature.</p>
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15 pages, 4009 KiB  
Article
Simulation and Application of a New Type of Energy-Saving Steel Claw for Aluminum Electrolysis Cells
by Jinfeng Han, Bing Feng, Zejun Chen, Zhili Liang, Yuran Chen and Xuemin Liang
Sustainability 2024, 16(18), 8061; https://doi.org/10.3390/su16188061 (registering DOI) - 14 Sep 2024
Viewed by 261
Abstract
Aluminum electrolysis is a typical industry with high energy consumption, and the energy saving of aluminum electrolysis cells is conducive to the sustainable development of the ecological environment. The current density distribution on the steel claws of conventional aluminum electrolysis cells is uneven, [...] Read more.
Aluminum electrolysis is a typical industry with high energy consumption, and the energy saving of aluminum electrolysis cells is conducive to the sustainable development of the ecological environment. The current density distribution on the steel claws of conventional aluminum electrolysis cells is uneven, resulting in a large amount of power loss. Therefore, a new type of current-equalized steel claw (CESC) is designed in this paper. The ANSYS simulation study shows that the CESC can achieve a more uniform current density distribution and reduce the voltage drop by about 36 mV compared with the traditional steel claw (TSC). In addition, the use of CESC optimizes the temperature distribution of the steel claws and reduces the risk of cracking and deformation. The results of the industrial application tests are highly consistent with the simulation results, confirming the accuracy of the simulation results. The economic benefit analysis shows that using CESC saves 114.1 kWh of electricity per ton of aluminum produced. If this technology can be promoted throughout China, it is expected to save up to 4.75 billion kWh of electricity annually. The development of CESC is promising and of great significance for improving the overall technical level of the aluminum electrolysis industry. Full article
(This article belongs to the Special Issue Sustainable Steel Construction)
22 pages, 1421 KiB  
Article
Experimental and Numerical Study on the Performance of Steel–Coarse Aggregate Reactive Powder Concrete Composite Beams with Uplift-Restricted and Slip-Permitted Connectors under Negative Bending Moment
by Xuan-Yang Zhong, Liang-Dong Zhuang, Ran Ding and Mu-Xuan Tao
Buildings 2024, 14(9), 2913; https://doi.org/10.3390/buildings14092913 (registering DOI) - 14 Sep 2024
Viewed by 226
Abstract
An innovative form of steel–concrete composite beam, the steel–coarse aggregate reactive powder concrete (CA-RPC) composite beam with uplift-restricted and slip-permitted (URSP) connectors, is introduced in this paper. The aim is to enhance the cracking resistance under negative bending moments, which is a difficult [...] Read more.
An innovative form of steel–concrete composite beam, the steel–coarse aggregate reactive powder concrete (CA-RPC) composite beam with uplift-restricted and slip-permitted (URSP) connectors, is introduced in this paper. The aim is to enhance the cracking resistance under negative bending moments, which is a difficult problem for traditional composite beams, and to make the cost lower than using ordinary reactive powder concrete (RPC). An experimental investigation of the behavior of six specimens of simply supported steel–CA-RPC composite beams with URSP connectors under negative bending moments is presented in this paper. The test results validated that the cracking load of steel–CA-RPC composite beams could be approximately three times that of the ordinary steel–concrete composite beams while the bearing capacity and stiffness are almost the same. A numerical model, using the concrete damaged plasticity (CDP) model to simulate the behavior of the CA-RPC material, was proposed and successfully calculated the overall load–displacement relationship of the composite beams with sufficient accuracy compared with the experimental results, and the distribution of cracks and the failure mode of the beams could also be captured by this model. Furthermore, a parametric analysis was carried out to find out how the application of prestress, CA-RPC, and URSP connectors could affect the cracking resistance of the composite beams, and the results indicated that using CA-RPC and prestress made the main contributions and that the usage of URSP could boost the effect of the other two factors. The plastic resistance moment of the beams was also compared with the calculation results using the methods introduced in Eurocode 4, and it was proved that the calculation results were lower than the experimental results by approximately 10%, which meant that the method was reliable for this kind of composite beam. Full article
(This article belongs to the Special Issue High-Performance Steel–Concrete Composite/Hybrid Structures)
15 pages, 3643 KiB  
Article
Deconvolution-Based System Identification and Finite Element Model Calibration of the UCLA Factor Building
by Fei Wang, Jiemei Ma, Xiandong Kang, Qixuan Liu and Hongyu Chen
Buildings 2024, 14(9), 2910; https://doi.org/10.3390/buildings14092910 (registering DOI) - 14 Sep 2024
Viewed by 188
Abstract
Analysis of wave propagation within buildings in response to earthquakes enables the tracking of changes in dynamic characteristics using impulse response functions. The velocity of traveling shear waves and the intrinsic attenuation of buildings can be retrieved, providing valuable input for system identification. [...] Read more.
Analysis of wave propagation within buildings in response to earthquakes enables the tracking of changes in dynamic characteristics using impulse response functions. The velocity of traveling shear waves and the intrinsic attenuation of buildings can be retrieved, providing valuable input for system identification. The Factor Building at the University of California, Los Angeles campus (henceforth referred to as the UCLA Factor Building), an instrumented 15-story steel moment frame structure, is selected for dynamic response characterization. Shear wave travel time and attenuation are computed from wave propagation using seismic interferometry applied to recorded motions, with deconvolved waves used to compute these parameters. In this study, the natural logarithm of the envelopes of waveforms deconvolved with the basement signal provided the measure of attenuation. Additionally, the waveforms deconvolved with the basement motion, indicating the building’s fundamental mode. The frequency and time decay further constrained the shear velocity and attenuation. Shear velocity was determined using arrival times measured from deconvolved waves, resulting in an average velocity of 147.1 m/s. The observed quality factor was 10.8, with a corresponding damping ratio of 5%. The shear wave velocity and damping ratio estimates derived from deconvolved waves showed consistency with those obtained from basement deconvolved waveforms. This consistency validates wave deconvolution as an effective method for isolating building response from excitation and ground coupling. By incorporating the resonant frequencies and damping ratios derived from previous analyses into a refined element model, this study underscores the potential of wave deconvolution for extracting building dynamic characteristics, thereby enhancing our understanding of their responses to earthquakes. Full article
(This article belongs to the Section Building Structures)
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<p>The flowchart for wave deconvolution analysis and model calibration.</p>
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<p>(<b>a</b>) Front Elevation of the Factor Building. (<b>b</b>) Typical plan view for Floors B1 to 9. (<b>c</b>) Typical plan view for Floors 10 to 15.</p>
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<p>(<b>a</b>) Front Elevation of the Factor Building. (<b>b</b>) Typical plan view for Floors B1 to 9. (<b>c</b>) Typical plan view for Floors 10 to 15.</p>
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<p>(<b>a</b>) Layout of sensors instrumented in the UCLA Factor Building. (<b>b</b>) East–west (EW) direction acceleration waveforms recorded in the Parkfield earthquake. (<b>c</b>) North—South (NS) direction acceleration waveforms.</p>
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<p>(<b>a</b>) Deconvolved waveforms with the signal recorded at the basement. (<b>b</b>) Deconvolved waveforms with the signal recorded at the roof and peak values of upward- and downward-propagating waves depicted with red circles for upward-propagating waves and green circles for downward-propagating waves.</p>
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<p>(<b>a</b>) Fourier spectra for the deconvolved waveforms at all the floors in <a href="#buildings-14-02910-f003" class="html-fig">Figure 3</a>a. (<b>b</b>) The travel time with distance in the east—west direction.</p>
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<p>Shear wave velocities with floor number. The shear wave velocity becomes larger at Floor 10 where the plane size extends outward.</p>
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<p>(<b>a</b>) The natural logarithm of these values is used to estimate the attenuation with a set of the best fitted lines. Between 1 and 13 s, the logarithm decays linearly with time. (<b>b</b>) The natural logarithm of the ratio of the amplitudes of the upward- and downward-propagating waves in the EW direction in <a href="#buildings-14-02910-f004" class="html-fig">Figure 4</a>b as a function of the two-way distance to the roof indicated with red solid circles.</p>
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<p>(<b>a</b>) The first nine modes for the Factor Building in two horizontal and vertical directions. (<b>b</b>) Shapes for the 1st and 2nd mode obtained from recorded earthquake data and simulated data. The discrepancies are negligible.</p>
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<p>(<b>a</b>) The Rayleigh damping curves for the numerical model. (<b>b</b>) Relative displacement calibration between the recorded data and the computed data. They are nearly consistent in frequencies and amplitudes.</p>
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31 pages, 15968 KiB  
Article
Study on the Bond Performance of Epoxy Resin Concrete with Steel Reinforcement
by Peiqi Chen, Yueqiang Li, Xiaojie Zhou, Hao Wang and Jie Li
Buildings 2024, 14(9), 2905; https://doi.org/10.3390/buildings14092905 (registering DOI) - 14 Sep 2024
Viewed by 184
Abstract
Abstract: Epoxy resin concrete, characterized by its superior mechanical properties, is frequently utilized for structural reinforcement and strengthening. However, its application in structural members remains limited. In this paper, the bond–slip behavior between steel reinforcement and epoxy resin concrete was investigated using a [...] Read more.
Abstract: Epoxy resin concrete, characterized by its superior mechanical properties, is frequently utilized for structural reinforcement and strengthening. However, its application in structural members remains limited. In this paper, the bond–slip behavior between steel reinforcement and epoxy resin concrete was investigated using a combination of experimental research and finite element analysis, with the objective of providing data support for substantiating the expanded use of epoxy resin concrete in structural members. The research methodology included 18 center-pullout tests and 14 finite element model calculations, focusing on the effects of variables such as epoxy resin concrete strength, steel reinforcement strength, steel reinforcement diameter and protective layer thickness on bond performance. The results reveal that the bond strength between epoxy resin concrete and steel reinforcement significantly surpasses that of ordinary concrete, being approximately 3.23 times higher given the equivalent strength level of the material; the improvement in the strength of both the epoxy resin concrete and steel reinforcement are observed to marginally increase the bond stress. Conversely, an increase in the diameter of the steel reinforcement and a reduction in the thickness of the protective layer of the concrete can lead to diminished bond stress and peak slip. Particularly, when the steel reinforcement strength is below 500 MPa, it tends to reach its yield strength and may even detach during the drawing process, indicating that the yielding of the steel reinforcement occurs before the loss of bond stress. In contrast, for a steel reinforcement strength exceeding 500 MPa, yielding does not precede bond stress loss, resulting in a distinct form of failure described as scraping plough type destruction. Compared to ordinary concrete, the peak of the epoxy resin concrete and steel reinforcement bond stress–slip curve is more pointed, indicating a rapid degradation to maximum bond stress and exhibiting a brittle nature. Overall, these peaks are sharper than those of ordinary concrete, indicating a rapid decline in bond stress post-peak, reflective of its brittle characteristics. Full article
19 pages, 14430 KiB  
Article
The Preparation of MoS2/Metal Nanocomposites Functionalized with N-Oleoylethanolamine: Application as Lubricant Additives
by Yaping Xing, Zhiguo Liu, Weiye Zhang, Zhengfeng Jia, Weifang Han, Jinming Zhen and Ran Zhang
Lubricants 2024, 12(9), 319; https://doi.org/10.3390/lubricants12090319 (registering DOI) - 14 Sep 2024
Viewed by 292
Abstract
In this study, MoS2 nanosheets have been prepared and treated ultrasonically with silver ammonia solutions. The MoS2/Ag precursor was reduced using dopamine (DA) as reducing and linking agent at room temperature, and it was subjected to a hydrothermal treatment to [...] Read more.
In this study, MoS2 nanosheets have been prepared and treated ultrasonically with silver ammonia solutions. The MoS2/Ag precursor was reduced using dopamine (DA) as reducing and linking agent at room temperature, and it was subjected to a hydrothermal treatment to produce MoS2/Ag nanocomposites (denoted as MoAg). The MoAg samples were functionalized with N-oleoylethanolamine to improve dispersion in the base oil component of additives. Use of the functionalized MoAg (denoted as Fc-MoAg) as a lubricant additive for steel balls resulted in effective friction reduction and anti-wear. This work avoids ion exchange during exfoliation, and the Ag+ has been reduced to nano-silver particles by dopamine to enlarge the layer spaces of MoS2. Taking the case of lubrication with base oil containing Fc-Mo0.6Ag15, the wear scar diameters and coefficients of friction of the steel balls were 0.428 and 0.098 mm, respectively, which were about three-fifths base oil. In addition, MoS2/Cu and MoS2/Ni nanocomposites were synthesized and the tribological properties associated with steel/steel balls assessed. The results demonstrate that all MoS2/metal composites exhibit enhanced tribological behavior in the steel/steel pair tests. Both nanocomposite synergy and the tribofilm containing sulfide, oxide, carbide, and other compounds play important roles in achieving reduced friction and improved anti-wear. The friction and wear properties of base oil containing Fc-MoAg and commercial additives were evaluated using a four-ball wear tester with steel/steel, steel/zirconia and zirconia/zirconia pairs. The base oil containing Fc-MoAg delivered smaller coefficients of friction (COFs) and/or scarring groove depths than those observed with the use of pure base oil and base oil containing commercial additives. Full article
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<p>(<b>a</b>) Schematic illustration of the synthesis process of Fc-MoAg; (<b>b</b>) sizes of Fc-MoAg in base oil after 0 day, 15 days, and 60 days.</p>
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<p>FE-SEM images of MoS<sub>2</sub> (<b>a</b>,<b>b</b>), exfoliated MoS<sub>2</sub> (<b>c</b>,<b>d</b>) and MoAg (<b>e</b>,<b>f</b>); TEM images of MoAg (<b>g</b>,<b>h</b>).</p>
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<p>SEM image (<b>a</b>), EDS elemental maps and EDS analysis of MoAg (160 °C) (<b>b</b>–<b>h</b>).</p>
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<p>(<b>a</b>) WSD–concentration curves, (<b>b</b>) COF–concentration curves for BO containing Fc–Mo<sub>x</sub>Ag<sub>20</sub> with different MoS<sub>2</sub> contents and (<b>c</b>) COF–time curves for BO and BO containing Fc–Mo<sub>x</sub>Ag<sub>20</sub> with different MoS<sub>2</sub> contents (concentration: 1.0 wt.%), respectively.</p>
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<p>(<b>a</b>) WSD–concentration curves, (<b>b</b>) COF–concentration curves for BO containing Fc-Mo<sub>0.6</sub>Ag<sub>y</sub> with different volumes of silver ammonia and (<b>c</b>) COF–time curves for BO and BO containing Fc-Mo<sub>0.6</sub>Ag<sub>y</sub> with different volumes of silver ammonia (concentration: 1.5 wt.%), respectively.</p>
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<p>(<b>a</b>) WSD–concentration curves, (<b>b</b>) COF–concentration curves for BO containing functionalized Mo<sub>0.6</sub>Ag<sub>0</sub>, Mo<sub>0</sub>Ag<sub>15</sub>, and Mo<sub>0.6</sub>Ag<sub>15</sub> and (<b>c</b>) COF–time curves for BO and BO containing functionalized Mo<sub>0.6</sub>Ag<sub>0</sub>, Mo<sub>0</sub>Ag<sub>15</sub>, and Mo<sub>0.6</sub>Ag<sub>15</sub> (concentration: 1.5 wt.%), respectively.</p>
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<p>(<b>a</b>) WSD–concentration curves, (<b>b</b>) COF–concentration curves for BO containing functionalized Mo0.6Ag15 with or without hydrothermal treatment and (<b>c</b>) COF–time curves for BO and BO containing functionalized Mo0.6Ag15 with or without hydrothermal treatment (concentration: 1.5 wt.%), respectively.</p>
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<p>(<b>a</b>) WSD–concentration curves, (<b>b</b>) COF–concentration curves for steel balls lubricated with BO containing functionalized Mo<sub>0.6</sub>Ag<sub>15</sub> and Mo<sub>0.6</sub>/Ag<sub>15,</sub> and (<b>c</b>) COF–time curves for steel balls lubricated with BO and BO containing functionalized Mo<sub>0.6</sub>Ag<sub>15</sub> and Mo<sub>0.6</sub>/Ag<sub>15</sub> (concentration: 1.5 wt.%), respectively.</p>
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<p>XRD patterns (<b>a</b>–<b>c</b>) for bulk MoS<sub>2</sub> before and after exfoliation.</p>
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<p>XRD patterns (<b>a</b>–<b>c</b>) for MoAg synthesized with and without hydrothermal treatment.</p>
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<p>Raman spectra (<b>a</b>,<b>b</b>) of Mo<sub>0.6</sub>Ag<sub>15</sub> before and after hydrothermal treatment.</p>
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<p>The optical images, 3D profile images, SEM images and cross-sectional curves of the worn surfaces lubricated with base oil without (<b>a</b>–<b>c</b>) and with (<b>d</b>–<b>g</b>) additives, respectively; the XPS spectra of worn surfaces lubricated with BO-c-Mo<sub>0.6</sub>Ag<sub>15</sub> (<b>h</b>–<b>n</b>).</p>
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<p>The optical images, 3D profile images, SEM images and cross-sectional curves of the worn surfaces lubricated with base oil without (<b>a</b>–<b>c</b>) and with (<b>d</b>–<b>g</b>) additives, respectively; the XPS spectra of worn surfaces lubricated with BO-c-Mo<sub>0.6</sub>Ag<sub>15</sub> (<b>h</b>–<b>n</b>).</p>
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<p>COF–time curves, corresponding 3D profile images and cross-sectional curves of the worn surfaces for lubrication using base oil with commercial additives (11.5 wt.%), and with/without Fc-Mo<sub>0.6</sub>Ag<sub>15</sub> (wt. 2.0%) in the case of (<b>a</b>) steel/steel, (<b>b</b>) steel/zirconia, and (<b>c</b>) zirconia/zirconia pairs, respectively.</p>
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<p>COF–time curves, corresponding 3D profile images and cross-sectional curves of the worn surfaces for lubrication using base oil with commercial additives (11.5 wt.%), and with/without Fc-Mo<sub>0.6</sub>Ag<sub>15</sub> (wt. 2.0%) in the case of (<b>a</b>) steel/steel, (<b>b</b>) steel/zirconia, and (<b>c</b>) zirconia/zirconia pairs, respectively.</p>
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<p>The sketch map of friction and wear mechanism.</p>
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21 pages, 4955 KiB  
Article
Efficient Phase Segmentation of Light-Optical Microscopy Images of Highly Complex Microstructures Using a Correlative Approach in Combination with Deep Learning Techniques
by Björn-Ivo Bachmann, Martin Müller, Marie Stiefel, Dominik Britz, Thorsten Staudt and Frank Mücklich
Metals 2024, 14(9), 1051; https://doi.org/10.3390/met14091051 (registering DOI) - 14 Sep 2024
Viewed by 181
Abstract
Reliable microstructure characterization is essential for establishing process–microstructure–property links and effective quality control. Traditional manual microstructure analysis often struggles with objectivity, reproducibility, and scalability, particularly in complex materials. Machine learning methods offer a promising alternative but are hindered by the challenge of assigning [...] Read more.
Reliable microstructure characterization is essential for establishing process–microstructure–property links and effective quality control. Traditional manual microstructure analysis often struggles with objectivity, reproducibility, and scalability, particularly in complex materials. Machine learning methods offer a promising alternative but are hindered by the challenge of assigning an accurate and consistent ground truth, especially for complex microstructures. This paper introduces a methodology that uses correlative microscopy—combining light optical microscopy, scanning electron microscopy, and electron backscatter diffraction (EBSD)—to create objective, reproducible pixel-by-pixel annotations for ML training. In a semi-automated manner, EBSD-based annotations are employed to generate an objective ground truth mask for training a semantic segmentation model for quantifying simple light optical micrographs. The training masks are directly derived from raw EBSD data using modern deep learning methods. By using EBSD-based annotations, which incorporate crystallographic and misorientation data, the correctness and objectivity of the training mask creation can be assured. The final approach is capable of reproducibly and objectively differentiating bainite and martensite in optical micrographs of complex quenched steels. Through the reduction in the microstructural evaluation to light optical micrographs as the simplest and most widely used method, this way of quantifying microstructures is characterized by high efficiency as well as good scalability. Full article
(This article belongs to the Special Issue Machine Learning Models in Metals)
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<p>Representation of the same section of a bainitic–martensitic microstructure using correlative microscopy. Shown are the EBSD IQ (<b>a</b>), the corresponding SEM (<b>b</b>), as well as LOM (<b>c</b>) image and misorientation information (<b>d</b>) using characteristic boundaries (&gt;2°—red, &gt;5°—green, &gt;15°—blue). Bainitic areas can be better distinguished from their martensitic counterparts, particularly due to the complementary EBSD information. Bainitic domains tendentially have a higher IQ (=brighter) and lower misorientation densities (red arrows).</p>
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<p>Correlative recordings of a highly complex quenched steel with bainitic (blue) and martensitic (yellow) regions (in (<b>d</b>,<b>e</b>)). Correspondingly isolated EBSD measured variables IQ (<b>a</b>), CI (<b>b</b>), and KAM first order (<b>c</b>), as well as the corresponding superposition of these three (<b>d</b>) in addition to the corresponding LOM (<b>e</b>), as well as the SEM (<b>f</b>) image after corresponding contrasting of the microstructures with Nital.</p>
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<p>The partial annotation (martensite—yellow, bainite—blue, unlabeled—white) (<b>d</b>) as overlays with respective EBSD mapping ((<b>a</b>) IQ, (<b>b</b>) CI, (<b>c</b>) KAM (colors of the mask adjusted for clarity—red tone as result of the overlay of the yellow mask with the KAM colorcode)), as well as with micrographs (SEM (<b>e</b>) and LOM (<b>f</b>)). Shown is the same sample section as in <a href="#metals-14-01051-f002" class="html-fig">Figure 2</a>.</p>
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<p>Schematic illustration of the used U-Net architecture [modified [<a href="#B58-metals-14-01051" class="html-bibr">58</a>]] with ImageNet pre-trained InceptionV3 encoder. Each individual EBSD channel (IQ, CI, and KAM) is concatenated to an RGB-like image after normalization to feed into U-Net. During the training process, the model learns the characteristic features of each individual class (martensite—yellow and bainite—blue). The white, unlabeled regions from the ground truth masks do not influence the learning process. For inference, the segmentation results are filtered by a confidence threshold of 70% (red) in order to create more meaningful results. As visible, the model is able to predict unlabeled regions. However, the loss function “L” only considers the labeled pixels during calculation by comparing the unfiltered prediction and ground truth mask during training.</p>
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<p>Segmentation result based on EBSD data after applying the 70% confidence threshold (<b>a</b>), with respective smoothing using the median filter (<b>b</b>). This image is subsequently used to train the segmentation model based on LOM images as an input, with blue representing bainite, yellow martensite, and red the unlabeled pixel, respectively. LOM is overlayed with an automatically generated training mask (<b>c</b>). No wrong labels could be identified using the correlative information. However, the confidence threshold of 75% is intentionally set conservatively in order to maintain a high level of objectivity and assurance in the labels. Red pixels correspond to confidence filtered regions.</p>
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<p>Segmentation results of the presented model using the EBSD data include a 0.5 confidence threshold (<b>a</b>) and 0.7 (<b>d</b>) after applying the median filter (bainite—blue, martensite—yellow, filtered—red). (<b>b</b>) shows the validation mask, which was partially annotated, and (<b>e</b>) as an overlay between the 0.7 threshold result and the EBSD input array consisting of IQ, CI, and KAM. (<b>c</b>) and (<b>f</b>) also show the post-processed segmentation result as an overlay with LOM and SEM, respectively.</p>
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<p>Magnification of an unclear area (red ellipsis) from <a href="#metals-14-01051-f006" class="html-fig">Figure 6</a>. Input array consisting of IQ, CI, and KAM (<b>a</b>), as well as overlay with post-processed prediction (<b>b</b>) (blue—bainite, yellow—martensite, filtered—red) and correlative high-resolution SEM image with corresponding overlaid prediction for clarification (<b>c</b>).</p>
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<p>Correlative EBSD input array overlaid with the corresponding post-processed prediction of the EBSD UNet model (blue—bainite, yellow—martensite, filtered—red) (<b>a</b>). The corresponding mask (<b>d</b>) served as the ground truth for training the LOM images (<b>b</b>). (<b>e</b>) shows the post-processed (analogous to EBSD post-processing) prediction of the trained LOM UNet. (<b>c</b>) displays the overlaid representation of this mask with correlating LOM input for clarification. A better assessment of the LOM-based result can be made using the high-resolution SEM image (<b>f</b>).</p>
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<p>Shown are the segmentation of the LOM-based model (<b>a</b>) and the EBSD-based model (<b>b</b>) for the identical ROI of the withheld sample. (<b>c</b>) shows the oppositely classified pixels between (<b>a</b>) and (<b>b</b>) (orange). A closer look at the underlying correlative data (left EBSD, middle SEM, right LOM) of these misclassified areas (colored squares) provides information about possible reasons for the misclassifications. The discrepancy areas are marked in orange in the respective LOM.</p>
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26 pages, 6030 KiB  
Article
Research on the Deformation Control Measures during the Construction Period of Super High-Rise Buildings with an Asymmetric Plan
by Hua-Ping Wang and Yi-Qing Xiao
Buildings 2024, 14(9), 2904; https://doi.org/10.3390/buildings14092904 (registering DOI) - 14 Sep 2024
Viewed by 174
Abstract
Based on the Guangzhou Business Center project, a typical super high-rise building with an asymmetric plan, taking the construction speed, closure time of mega braces and belt trusses as influencing factors, a parametric analysis on its lateral and vertical deformations, as well as [...] Read more.
Based on the Guangzhou Business Center project, a typical super high-rise building with an asymmetric plan, taking the construction speed, closure time of mega braces and belt trusses as influencing factors, a parametric analysis on its lateral and vertical deformations, as well as the maximum stress of key structural members was conducted. The analysis results indicated that the construction speed had a relatively small impact on the deformation and the maximum stress of key members. However, synchronous closure of belt truss compared with the delayed closure would result in smaller horizontal and vertical deformation differences, as well as the stress of belt truss. Meanwhile, the closure timing of the mega braces had little influence on the vertical deformation difference and the stress of belt truss. And the earlier the closure, the smaller the horizontal drift ratio, the greater the maximum stress of the mega braces. Further, deformation control measurements were brought forward. On the one hand, FEM simulation was carried out according to the above construction suggestions. On the other hand, real-time monitoring was also used. Finally, by comparing both results, proposed construction deformation control measures and simulation methods were verified. Full article
(This article belongs to the Topic Resilient Civil Infrastructure)
20 pages, 7676 KiB  
Article
Study on the Dynamic Response of Mooring System of Multiple Fish Cages under the Combined Effects of Waves and Currents
by Fuxiang Liu, Zhentao Jiang, Tianhu Cheng, Yuwang Xu, Haitao Zhu, Gang Wang, Guoqing Sun and Yuqin Zhang
J. Mar. Sci. Eng. 2024, 12(9), 1648; https://doi.org/10.3390/jmse12091648 (registering DOI) - 14 Sep 2024
Viewed by 170
Abstract
Deep-sea aquaculture can alleviate the spatial and environmental pressure of near-shore aquaculture and produce higher quality aquatic products, which is the main development direction of global aquaculture. The coastline of China is relatively flat, with aquaculture operations typically operating in sea areas with [...] Read more.
Deep-sea aquaculture can alleviate the spatial and environmental pressure of near-shore aquaculture and produce higher quality aquatic products, which is the main development direction of global aquaculture. The coastline of China is relatively flat, with aquaculture operations typically operating in sea areas with water depths of approximately 30–50 m. However, with frequent typhoons and poor sea conditions, the design of mooring system has always been a difficult problem. This paper investigated the multiple cages, considering two layouts of 1 × 4 and 2 × 2, and proposed three different mooring system design schemes. The mooring line tension of the mooring systems under the self-storage condition was compared, and it was observed whether the mooring line accumulation and the contact between the mooring line and the steel structure occurred on the leeward side. Additionally, flexible net models were compared with rigid net models to evaluate the impact of net deformation on cage movement and mooring line tension. Finally, based on the optimal mooring design, the dynamic response of the mooring system under irregular wave conditions was analyzed and studied, providing important reference for the safety and economic design of the mooring system of multiple fish cages. Full article
(This article belongs to the Special Issue New Techniques and Equipment in Large Offshore Aquaculture Platform)
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<p>Numerical approach for hydrodynamic analysis of the fish cages.</p>
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<p>Lumped mass method [<a href="#B29-jmse-12-01648" class="html-bibr">29</a>].</p>
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<p>Single cage numerical calculation model.</p>
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<p>Scheme 1: Layout of 1 × 4 cages and design of mooring system.</p>
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<p>Scheme 2: Layout of 1 × 4 cages and design of inclined mooring system.</p>
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<p>Scheme 2: Layout of 1 × 4 cages and design of inclined mooring system.</p>
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<p>Scheme 3: Layout of 2 × 2 cages and design of mooring system.</p>
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<p>Scheme 1 Maximum mooring line tension under 0° wave-current incidence.</p>
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<p>Deformation of nets in Scheme 1.</p>
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<p>Scheme 1. Maximum mooring line tension under 45° wave-current incidence.</p>
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<p>Scheme 1. Maximum mooring line tension under 90° wave-current incidence.</p>
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<p>Scheme 1. Side view of cable status when large displacement occurs (0° wave-current incidence).</p>
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<p>Scheme 2. Maximum mooring line tension under 0° wave-current incidence.</p>
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<p>Scheme 2. Maximum mooring line tension under 45° wave-current incidence.</p>
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<p>Scheme 2. Maximum mooring line tension under 90° wave-current incidence.</p>
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<p>Scheme 2. Side view of cable status when large displacement occurs (90° wave-current incidence).</p>
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<p>Scheme 3. Maximum mooring line tension under 0° wave-current incidence.</p>
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<p>Scheme 3. Maximum mooring line tension under 45° wave-current incidence.</p>
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<p>Response to the surge motion.</p>
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<p>Heave motion response.</p>
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<p>Heave motion response.</p>
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<p>Maximum cable tension.</p>
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<p>Motion of Fish Cage1.</p>
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<p>Comparison of motion spectrum.</p>
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<p>Tension on mooring chain and connect cable.</p>
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<p>Tension spectrum of mooring chain and connecting cable.</p>
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<p>Fitting of Gumbel distribution for mooring line at 0° wave-current incidence direction.</p>
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<p>Fitting of Gumbel distribution for mooring line at 45° wave-current incidence direction.</p>
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