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Keywords = wire arc additive manufacturing

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16 pages, 11669 KiB  
Article
Deposition Strategies for Bar Intersections Using Dot-by-Dot Wire and Arc Additive Manufacturing
by Niccolò Grossi, Flavio Lazzeri and Giuseppe Venturini
J. Manuf. Mater. Process. 2025, 9(3), 77; https://doi.org/10.3390/jmmp9030077 - 27 Feb 2025
Viewed by 214
Abstract
Dot-by-dot Wire and Arc Additive Manufacturing (WAAM) is a promising technique for producing large-scale lattice structures, offering significant benefits in terms of deposition rate and material utilization. This study explores strategies for fabricating bar intersections using the dot-by-dot WAAM technology, focusing on creating [...] Read more.
Dot-by-dot Wire and Arc Additive Manufacturing (WAAM) is a promising technique for producing large-scale lattice structures, offering significant benefits in terms of deposition rate and material utilization. This study explores strategies for fabricating bar intersections using the dot-by-dot WAAM technology, focusing on creating robust and predictable structures without requiring parameter modifications or real-time monitoring during the deposition. Two different deposition strategies were proposed, that can be, at least geometrically, applied to a general intersection with multiple bars with different angles. In this work such strategies were only experimentally tested on two-bar intersections, assessing their performance in terms of geometrical accuracy, symmetry, and material efficiency. Strategies which utilize layer-by-layer deposition with multiple overlapping dots, called B here, demonstrated the best results in terms of the geometrical features in the intersection zone, assessed by different metrics obtained through an analysis of pictures, such as low asymmetry and high material volume in the intersection zone. In addition, the findings suggest that removing cooling pauses during the deposition of multiple dots on the same layer slightly improves the joint by minimizing excess material buildup. The proposed approach offers a scalable framework for optimizing intersection deposition, paving the way for improved large-scale metal lattice structure manufacturing. Full article
(This article belongs to the Special Issue Large-Scale Metal Additive Manufacturing)
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<p>Schematic representation of the intersection zone for the investigated configuration, bisector is shown as red line.</p>
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<p>Strategy A: (<b>a</b>) R 100%; (<b>b</b>) R 50%, bisector is shown as red line.</p>
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<p>Strategy B: (<b>a</b>) B1; (<b>b</b>) B2, bisector is shown as red line.</p>
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<p>X-joint (case study): (<b>a</b>) A–R 100%, (<b>b</b>) A–R 50%, (<b>c</b>) B1–M0.6.</p>
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<p>Two-bar joint: (<b>a</b>) A–R 100%, (<b>b</b>) A–R 50%, (<b>c</b>) B1–M0.6.</p>
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<p>Three-bar joint: (<b>a</b>) A–R 50%, (<b>b</b>) B1–M0.6.</p>
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<p>Tetrahedron: (<b>a</b>) A–R 50%; (<b>b</b>) B1–M0.6.</p>
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<p>Unit cell: (<b>a</b>) A–R 50%; (<b>b</b>) B1–M0.6.</p>
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<p>Structure: (<b>a</b>) A–R 50%; (<b>b</b>) B1–M0.6.</p>
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<p>Metrics used to assess the effectiveness of the joint: (<b>a</b>) convergent specimen; (<b>b</b>) convergent–divergent specimen.</p>
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<p>Example of identification of symmetry metric c.</p>
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<p>Desired geometry of the selected two-bar joint: (<b>a</b>) convergent; (<b>b</b>) convergent–divergent.</p>
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<p>Example of picture analysis to identify metrics (id C_B1_0.6_P).</p>
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<p>Test id C_100 results.</p>
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<p>Convergent tests results for strategy A ids: (<b>a</b>) C_A_100; (<b>b</b>) C_A_75; (<b>c</b>) C_A_50; (<b>d</b>) C_A_25; (<b>e</b>) C_A_0.</p>
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<p>Convergent tests results for strategy B1 ids: (<b>a</b>) C_B1_0.9_P; (<b>b</b>) C_B1_0.8_P; (<b>c</b>) C_B1_0.7_P; (<b>d</b>) C_B1_0.6_P; (<b>e</b>) C_B1_0.7_NP; (<b>f</b>) C_B1_0.6_NP.</p>
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<p>Convergent tests results for strategy B2 ids: (<b>a</b>) C_B2_0.8_P; (<b>b</b>) C_B2_0.7_P; (<b>c</b>) C_B2_0.6_P; (<b>d</b>) C_B2_0.7_NP; (<b>e</b>) C_B2_0.6_NP.</p>
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<p>Convergent–divergent test results ids: (<b>a</b>) CD_A_75 (<b>b</b>) CD_A_50 (<b>c</b>) CD_B2_0.7_P (<b>d</b>) CD_B1_0.7_NP (<b>e</b>) CD_B2_0.6_NP.</p>
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<p>Strategy A convergent case results: (<b>a</b>) percentage error; (<b>b</b>) h and dc values.</p>
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<p>Strategy B1 convergent case results: (<b>a</b>) percentage error; (<b>b</b>) h and dc values respect to the desired value (h 37.64 mm, dc 7.96 mm).</p>
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<p>Strategy B2 convergent case results: (<b>a</b>) percentage error; (<b>b</b>) h and dc values with respect to the desired value (h 37.64 mm, dc 7.96 mm).</p>
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<p>Convergent–divergent case results: (<b>a</b>) percentage error; (<b>b</b>) h and dc values with respect to the desired value (h 69.28 mm, dc 8.03 mm).</p>
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12 pages, 10747 KiB  
Communication
Microstructure and Mechanical Properties of Inconel 718 Alloy Fabricated Using Wire Feeding Oscillated Double-Pulsed GTA-AM
by Gang Zhang, Cheng Zhang, Yu Shi and Ding Fan
Metals 2025, 15(3), 248; https://doi.org/10.3390/met15030248 - 26 Feb 2025
Viewed by 150
Abstract
To address anisotropy challenges in electric arc-based additive manufacturing of Inconel 718 alloy, this study develops a novel wire feeding oscillated double-pulsed gas tungsten arc welding additive manufacturing method (DP-GTA-AM) enabling precise thermal-mass transfer control. Series of crack-free thin-walled Inconel 718 alloy parts [...] Read more.
To address anisotropy challenges in electric arc-based additive manufacturing of Inconel 718 alloy, this study develops a novel wire feeding oscillated double-pulsed gas tungsten arc welding additive manufacturing method (DP-GTA-AM) enabling precise thermal-mass transfer control. Series of crack-free thin-walled Inconel 718 alloy parts were successfully obtained by this proposed approach, and the microstructure and mechanical properties of the parts were thoroughly studied. The results indicate that the microstructure changes from dendrites and cellular crystals in the bottom to equiaxed grains in the midsection and entirely equiaxed crystals in the top, resulting in notable grain refinement. With an average grain size of 61.76 ?m and an average length of 83.31 ?m of large angle grain boundaries, the density of the <001> direction reaches 19.45. The difference in tensile strength and ductility between the horizontal and the vertical directions decreases to 6.3 MPa and 0.38%, which significantly diminishes anisotropy. Fractographic analysis confirms quasi-cleavage failure with homogeneous dimple distribution, demonstrating effective anisotropy mitigation through controlled solidification dynamics. Full article
(This article belongs to the Special Issue Advance in Wire-Based Additive Manufacturing of Metal Materials)
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<p>Schematic diagram of wire feeding oscillated DP-GTAW AM.</p>
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<p>Experimental setup and measurement. (<b>a</b>) DP-GTAW AM system. (<b>b</b>) Tensile specimen size and sampling. (<b>c</b>) X-ray detection image of thin-walled component.</p>
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<p>Microtopography of AM sample manufactured by high pulse frequency 120 Hz. (<b>A</b>) OM image, (1) region 1; (2) region 2; (3) region 3. (<b>B</b>) SEM and EDS. (<b>C</b>) EBSD. (<b>D</b>) Pole images.</p>
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<p>Microtopography of AM sample manufactured by high pulse frequency 160 Hz. (<b>A</b>) OM image, (1) region 1; (2) region 2; (3) region 3. (<b>B</b>) SEM and EDS. (<b>C</b>) EBSD. (<b>D</b>) Pole images.</p>
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<p>Mechanical properties of the DP-GTAW-AM component. (<b>a</b>) Strain–stress curve, ultimate tensile strength and ductility. (<b>b</b>) Microhardness. (<b>c</b>,<b>d</b>) Horizontal and vertical fracture shape. (<b>e</b>,<b>f</b>) Horizontal and vertical dendrite tearing. The red arrow represents the direction of force action.</p>
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29 pages, 12675 KiB  
Article
Impact of Machining Parameters on Wire Arc Additively Manufactured Mild Steel Specimens of E6013 and E7018 Using an Electric Arc Heat Source
by Muhammad Muzamil, Nabeel Ahmed Siddiqui, Kamal Kumar, Ghulam Hussain, Mohammed Alkahtani and Mohsin Sattar
Crystals 2025, 15(3), 222; https://doi.org/10.3390/cryst15030222 - 26 Feb 2025
Viewed by 215
Abstract
This study investigates the machining parameters that affect the surface roughness of additively manufactured specimens employing wire arc additive manufacturing (WAAM) using electric arc welding as a heat source. The specimens were prepared using E6013 and E7018 filler rods for layered deposition on [...] Read more.
This study investigates the machining parameters that affect the surface roughness of additively manufactured specimens employing wire arc additive manufacturing (WAAM) using electric arc welding as a heat source. The specimens were prepared using E6013 and E7018 filler rods for layered deposition on a mild steel base plate. For the machining operation, two variable parameters, cutting speed and depth of cut, were selected and coded as high (480 RPM, 0.5 mm depth) and low (310 RPM, 0.25 mm depth) while keeping the feed rate constant. The study employed a 2k factorial design of experiment (DOE) using Minitab software to assess the impact of parameters and their levels on the output response of surface roughness. Analysis of variance (ANOVA) results show that cutting parameters like cutting speed and their interaction with the depth of cut significantly affect surface quality. The experimental data were also used to develop polynomial model response equations for predicting surface roughness. This study firmly demonstrates the critical role of machining parameters in enhancing the surface quality of low-cost additively manufactured components using an electric arc welding heat source. Full article
(This article belongs to the Special Issue Plastic Deformation and Welding on Metallic Materials)
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<p>A schematic representation of how relevant additive manufacturing methods are chosen based on technical requirements [<a href="#B8-crystals-15-00222" class="html-bibr">8</a>].</p>
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<p>Graphical illustration of methodological sequence.</p>
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<p>Pictorial view of layered structure deposition of filler wire from wire arc additive manufacturing (WAAM).</p>
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<p>Pictorial view of the deposition of an electrode employing E6013 and E7018 for the fabrication of specimens from SMAW.</p>
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<p>Machining operations of WAAM across different machining parameter settings.</p>
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<p>Plot illustrating the significance of factors affecting surface roughness.</p>
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<p>Pareto chart showing standardized effects on surface roughness.</p>
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<p>Residual plots illustrating deviations in surface roughness.</p>
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<p>Main effect factorial plots of E6013 for analyzing surface roughness.</p>
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<p>Interaction plot depicting factors influencing surface roughness.</p>
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<p>Contour plot of surface roughness vs. depth of cut (mm) and cutting speed (RPM) for E6013.</p>
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<p>Plot showing the significance of factors affecting surface roughness.</p>
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<p>Pareto chart displaying standardized effects on surface roughness.</p>
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<p>Residual plots depict deviations in surface roughness.</p>
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<p>Main effect factorial plots of surface roughness for E7018 electrode.</p>
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<p>Interaction plot showing the effects of parameters on surface roughness for E7018.</p>
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<p>Contour plot of surface roughness vs. depth of cut (mm) and cutting speed (RPM) for E7018.</p>
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<p>Stereo microscopy images of machining chips formed at (E6013) (<b>a</b>) S1: 480 RPM and 0.25 mm depth of cut; (<b>b</b>) S2: 480 RPM and 0.5 mm depth of cut; (<b>c</b>) S3: 310 RPM and 0.25 mm depth of cut; and (<b>d</b>) S4: 310 RPM and 0.5 mm depth of cut.</p>
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<p>Stereo microscopy images of machining chips formed at (E7018) (<b>a</b>) A1: 480 RPM and 0.25 mm depth of cut; (<b>b</b>) A2: 480 RPM and 0.5 mm depth of cut; (<b>c</b>) A3: 310 RPM and 0.25 mm depth of cut; and (<b>d</b>) A4: 310 RPM and 0.5 mm depth of cut.</p>
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17 pages, 3689 KiB  
Article
Application of Symmetric Neural Networks for Bead Geometry Determination in Wire and Arc Additive Manufacturing (WAAM)
by Aitor Fernández-Zabalza, Fernando Veiga, Alfredo Suárez, Virginia Uralde, Xabier Sandua and José Ramón Alfaro
Symmetry 2025, 17(3), 326; https://doi.org/10.3390/sym17030326 - 21 Feb 2025
Viewed by 182
Abstract
The accurate prediction of weld bead geometry is crucial for ensuring the quality and consistency of wire and arc additive manufacturing (WAAM), a specific form of directed energy deposition (DED) that utilizes arc welding. Despite advancements in process control, predicting the shape and [...] Read more.
The accurate prediction of weld bead geometry is crucial for ensuring the quality and consistency of wire and arc additive manufacturing (WAAM), a specific form of directed energy deposition (DED) that utilizes arc welding. Despite advancements in process control, predicting the shape and dimensions of weld beads remains challenging due to the complex interactions between process parameters and material behavior. This paper addresses this challenge by exploring the application of symmetrical neural networks to enhance the accuracy and reliability of geometric predictions in WAAM. By leveraging advanced machine learning techniques and incorporating the inherent symmetry of the welding process, the proposed models aim to precisely forecast weld bead geometry. The use of neuronal networks and experimental validation demonstrate the potential of symmetrical neural networks to improve prediction precision, contributing to more consistent and optimized WAAM outcomes. Full article
(This article belongs to the Section Engineering and Materials)
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<p>Macroscopic images of the bead’s cross-section: (<b>a</b>) bead geometry without annotations; (<b>b</b>) bead geometry with selected measurement indicators, including height (h<sub>0</sub>, h<sub>1</sub>, h<sub>2</sub>) and width (w<sub>0</sub>, w<sub>1</sub>, w<sub>2</sub>); and (<b>c</b>) detailed representation of the heat-affected zone (HAZ) and penetration area.</p>
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<p>Macroscopic images of all analyzed bead cross-sections: (<b>a</b>) Test 1, (<b>b</b>) Test 2, (<b>c</b>) Test 3, (<b>d</b>) Test 4, (<b>e</b>) Test 5, (<b>f</b>) Test 6, (<b>g</b>) Test 7, (<b>h</b>) Test 8, (<b>i</b>) Test 9.</p>
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<p>RSM of the bead cross-section areas: (<b>a</b>) bead area over the substrate, (<b>b</b>) HAZ, and (<b>c</b>) penetration area.</p>
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<p>Correlation matrix heatmap.</p>
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<p>Weld bead profile measured raw by profilometer and then treated to extract characteristic heights and widths, red dashed lines displayed on the right side of the image, in profile 5 of Test 7.</p>
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<p>Training and validation of the symmetric neural network by means of (<b>a</b>) a loss function and (<b>b</b>) MAE.</p>
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<p>Prediction results versus actual values in the case of the critical output variables: (<b>a</b>) bead area, (<b>b</b>) HAZ, and (<b>c</b>) penetration.</p>
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21 pages, 3622 KiB  
Article
Predictive Modelling of Weld Bead Geometry in Wire Arc Additive Manufacturing
by Kristijan Šket, Miran Brezočnik, Timi Karner, Rok Belšak, Mirko Ficko, Tomaž Vuherer and Janez Gotlih
J. Manuf. Mater. Process. 2025, 9(2), 67; https://doi.org/10.3390/jmmp9020067 - 19 Feb 2025
Viewed by 260
Abstract
This study investigates the predictive modelling of weld bead geometry in wire arc additive manufacturing (WAAM) through advanced machine learning methods. While WAAM is valued for its ability to produce large, complex metal parts with high deposition rates, precise control of the weld [...] Read more.
This study investigates the predictive modelling of weld bead geometry in wire arc additive manufacturing (WAAM) through advanced machine learning methods. While WAAM is valued for its ability to produce large, complex metal parts with high deposition rates, precise control of the weld bead remains a critical challenge due to its influence on mechanical properties and dimensional accuracy. To address this problem, this study utilized machine learning approaches—Ridge regression, Lasso regression and Bayesian ridge regression, Random Forest and XGBoost—to predict the key weld bead characteristics, namely height, width and cross-sectional area. A Design of experiments (DOE) was used to systematically vary the welding current and travelling speed, with 3D weld bead geometries captured by laser scanning. Robust data pre-processing, including outlier detection and feature engineering, improved modelling accuracy. Among the models tested, XGBoost provided the highest prediction accuracy, emphasizing its potential for real-time control of WAAM processes. Overall, this study presents a comprehensive framework for predictive modelling and provides valuable insights for process optimization and the further development of intelligent manufacturing systems. Full article
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<p>Materials and methods for modelling of weld bead geometry in wire arc additive manufacturing.</p>
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<p>The process of extracting weld bead seams from scanned point clouds.</p>
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<p>Summarized SHAP plot (<b>a</b>) and SHAP dependence plot for current (<b>b</b>) for mean weld bead height.</p>
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<p>Predicted vs. actual weld bead height, scatter plots for (<b>a</b>) the training set and (<b>b</b>) the predictions of the test set.</p>
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<p>Summarized SHAP plot (<b>a</b>) and SHAP dependence plot for current (<b>b</b>) for mean weld bead width.</p>
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<p>Predicted vs. actual weld bead width, scatter plots for (<b>a</b>) the training set and (<b>b</b>) the predictions of the test set.</p>
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<p>Summarized SHAP plot (<b>a</b>) and SHAP dependence plot for current (<b>b</b>) for mean weld cross-section area.</p>
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<p>Predicted vs. actual weld bead cross-section area, scatter plots for (<b>a</b>) the training set and (<b>b</b>) the predictions for the test set.</p>
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24 pages, 6650 KiB  
Article
Wire Arc Additive Manufacturing of Scalmalloy® (Al-Mg-Sc-Zr): Thermal Management Effects on Direct Age-Hardening Response
by Leandro João da Silva, Douglas Bezerra de Araújo, Ruham Pablo Reis, Frank Palm and Américo Scotti
Coatings 2025, 15(2), 237; https://doi.org/10.3390/coatings15020237 - 17 Feb 2025
Viewed by 245
Abstract
The thermal history of a part deposited via wire arc additive manufacturing (WAAM) and hence its as-built properties can vary significantly depending on the thermal management applied, especially for metallurgically complex materials. Thus, this work aimed to assess the feasibility of processing thin-walled [...] Read more.
The thermal history of a part deposited via wire arc additive manufacturing (WAAM) and hence its as-built properties can vary significantly depending on the thermal management applied, especially for metallurgically complex materials. Thus, this work aimed to assess the feasibility of processing thin-walled Scalmalloy® (Al-Mg-Sc-Zr) structures by WAAM while examining the effects of arc energy and heat dissipation on their response to direct age-hardening heat treatment (without solution annealing). As a complement, the geometry, porosity, and processing time of such parts were also analyzed. The walls were built via the cold metal transfer (CMT) deposition process with different arc energy levels in combination with near-immersion active cooling (NIAC) settings (as thermal management solution), as well as with natural cooling (NC), resulting overall in both low surface waviness and porosity levels. Based on hardness testing, the resultant Scalmalloy® direct-aging response (relative increase in hardness after direct age-hardening from WAAM as-built state) depended more on the arc energy per unit length of deposit applied. In contrast, the other thermal management approaches (NIAC or NC) helped in maintaining Sc in a supersaturated solid solution during deposition. Thus, Scalmalloy® strengthening was demonstrated as feasibly triggered by means of a post-WAAM direct age-hardening heat treatment solely. Additionally, in comparison with a thermally equivalent (same interpass temperature) condition based on NC, the NIAC technique allowed the achievement of such a positive result on direct-aging response with much shorter WAAM processing times, therefore improving productivity. Full article
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<p>Experimental rig used for WAAM of thin-walled Scalmalloy<sup>®</sup> structures. <b>left</b>: actual deposition setup; <b>right</b>: deposition representation.</p>
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<p>IR pyrometry arrangement used for monitoring the thermal features of the thin-walled Scalmalloy<sup>®</sup> preforms (water temperature monitoring used for assuring stable operation of the NIAC technique).</p>
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<p>Geometric features analyzed in the cross-sections of the preforms.</p>
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<p>Hardness measurement path applied in the cross-sections of the preforms.</p>
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<p>Correlation between WFS/TS ratio and AE level for the CMT deposition process as applied.</p>
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<p>Lateral surface aspect and cross-section view of each thin-walled Scalmalloy<sup>®</sup> preform built via WAAM with variation in the WFS/TS ratio (AE level) for the LEWD parameter fixed in 20 mm.</p>
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<p>Lateral surface aspect and cross-section view of each thin-walled Scalmalloy<sup>®</sup> preform built via WAAM with variation in the LEWD parameter for the WFS/TS ratio fixed in 12.5 (same AE level) (NC case included for comparison basis).</p>
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<p>Thermal effect measured by the trailing/leading IR pyrometer in the thin-walled Scalmalloy<sup>®</sup> preforms built via WAAM with different thermal management scenarios: (<b>a</b>) WFS/TS ratio (and AE level) variation (fixed LEWD value = 20 mm); (<b>b</b>) LEWD parameter variation (fixed WFS/TS ratio = 12.5 (same AE level)).</p>
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<p>Typical thermal history (measured by the fixed IR pyrometer) experienced by a given layer of the thin-walled Scalmalloy<sup>®</sup> preforms built via WAAM with the NIAC technique as new layers were sequentially added.</p>
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<p>Correlation between the peak temperature observed in the Scalmalloy<sup>®</sup> layer surveyed in <a href="#coatings-15-00237-f009" class="html-fig">Figure 9</a> and the distance from the top (last) layer of the respective preform as new layers were sequentially added.</p>
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<p>Typical correlation between the cooling rate and the peak temperature extracted from the thermal history of a Scalmalloy<sup>®</sup> layer as new layers were sequentially added (case surveyed in <a href="#coatings-15-00237-f009" class="html-fig">Figure 9</a> and <a href="#coatings-15-00237-f010" class="html-fig">Figure 10</a>).</p>
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<p>Effect of the WFS/TS ratio (and AE level) variation on the cooling rate of Scalmalloy<sup>®</sup> layers (considering peak temperatures of 650 °C) with the LEWD parameter fixed in 20 mm.</p>
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<p>Effect of the LEWD parameter variation on the cooling rate of Scalmalloy<sup>®</sup> layers (considering peak temperatures of 650 °C) with the WFS/TS ratio fixed in 12.5 (same AE level).</p>
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<p>Example of hardness profiles revealed along the height of thin-walled Scalmalloy<sup>®</sup> preforms built via WAAM under different thermal management conditions (but with the same WFS/TS ratio = 12.5 (same AE level)) both in the as-built and heat-treated states: (<b>a</b>) NIAC technique; (<b>b</b>) NC approach.</p>
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<p>Average hardness levels of the thin-walled Scalmalloy<sup>®</sup> preforms built via WAAM under different thermal management conditions measured both in the as-built and heat-treated states: (<b>a</b>) WFS/TS ratio (and AE level) variation (fixed LEWD value = 20 mm); (<b>b</b>) LEWD parameter variation (fixed WFS/TS ratio = 12.5 (same AE level)) (NC case included for comparison basis).</p>
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<p>Effect of the cooling rate (resulting from the thermal management conditions) on the direct-aging response of the thin-walled Scalmalloy<sup>®</sup> preforms built via WAAM: (<b>a</b>) WFS/TS ratio (and AE level) variation (fixed LEWD value = 20 mm); (<b>b</b>) LEWD parameter variation (fixed WFS/TS ratio = 12.5 (same AE level)) (NC case (red marker) included for comparison basis).</p>
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<p>The potential of the NIAC technique for modulating the cooling rate of a Scalmalloy<sup>®</sup> target wall width (EWW of 5 mm).</p>
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20 pages, 17189 KiB  
Article
Parametric Study on Investigations of GMAW-Based WAAM Process Parameters and Effect on Microstructure and Mechanical Properties of NiTi SMA
by Vatsal Vaghasia, Rakesh Chaudhari, Vivek K. Patel and Jay Vora
J. Manuf. Mater. Process. 2025, 9(2), 58; https://doi.org/10.3390/jmmp9020058 - 13 Feb 2025
Viewed by 404
Abstract
In the present study, an attempt was made to build a thin-walled structure consisting of 10 layers using nitinol wire on a titanium substrate via a gas–metal arc welding (GMAW)-based wire-arc additive manufacturing (WAAM) process. A thin-walled structure was fabricated by using nitinol [...] Read more.
In the present study, an attempt was made to build a thin-walled structure consisting of 10 layers using nitinol wire on a titanium substrate via a gas–metal arc welding (GMAW)-based wire-arc additive manufacturing (WAAM) process. A thin-walled structure was fabricated by using nitinol wire on a titanium substrate at the optimized parameters of a wire feed speed of 6 m/min, a travel speed of 12 mm/s, and a voltage of 20 V. In a microstructural study, the heat-affected zone was observed to have coarse grains and be columnar in shape, and the first layer exhibited a mix of dendritic structures. The mid-layers demonstrated a mix of coarse and fine columnar grains with dendritic colonies, while the last few layers demonstrated fairly equiaxed grains as well as a finer microstructure, as the cooling rates were very slow. The ultimate tensile strengths (UTSs) obtained at the bottom and top portions were found to be 536.22 MPa and 586.31 MPa. Elongation (EL) degrees of 10.72% and 11.57% were observed in the bottom and top portions, respectively. The fractography of the tensile specimen showed good toughness and ductility of the fabricated nitinol specimen. A microhardness examination showed a minimum value of 236.56 HV in the bottom layer and a maximum value of 316.78 HV in the topmost layer. Full article
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<p>The GMAW-based WAAM experimental setup.</p>
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<p>Determination of bead morphologies, BW and BH.</p>
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<p>Process chart of the HTS algorithm [<a href="#B44-jmmp-09-00058" class="html-bibr">44</a>].</p>
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<p>A 10-layered nitinol specimen fabricated by WAAM at optimized parameters.</p>
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<p>Testing locations of the built structure.</p>
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<p>Single-layer depositions along with cut cross-sections of depositions.</p>
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<p>Influences of WAAM variables on BH response.</p>
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<p>Influences of WAAM variables on BW response.</p>
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<p>Macrostructure of the built WAAM structure.</p>
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<p>Microstructures of (<b>a</b>) HAZ and initial layers, (<b>b</b>) middle layers, and (<b>c</b>) top layers of the built WAAM structure.</p>
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<p>Microstructures of (<b>a</b>) HAZ and initial layers, (<b>b</b>) middle layers, and (<b>c</b>) top layers of the built WAAM structure.</p>
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<p>Tensile test specimens (<b>a</b>) after fracture and (<b>b</b>) after fractography.</p>
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<p>Microhardness along the build direction for a WAAM structure of nitinol SMA.</p>
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17 pages, 7657 KiB  
Article
Microstructure, Thermal, and Mechanical Behavior of NiTi Shape Memory Alloy Obtained by Micro Wire and Arc Direct Energy Deposition
by Tadeu C. da Silva, Edwin Sallica-Leva, Emilio Rayón, Claudio T. Santos, João C. A. D. Filho, Neri Volpato, Dalton D. Lima, Paulo H. G. Dornelas, Sergio S. M. Tavares and Telmo G. Santos
J. Manuf. Mater. Process. 2025, 9(2), 57; https://doi.org/10.3390/jmmp9020057 - 13 Feb 2025
Viewed by 594
Abstract
Additive manufacturing (AM) is revolutionizing the fabrication of metallic components, offering significant potential to compete with or complement traditional casting, forging, and machining processes, and enabling the production of complex functional components. Recent advancements in AM technology have facilitated the processing of shape [...] Read more.
Additive manufacturing (AM) is revolutionizing the fabrication of metallic components, offering significant potential to compete with or complement traditional casting, forging, and machining processes, and enabling the production of complex functional components. Recent advancements in AM technology have facilitated the processing of shape memory alloys (SMAs) with functional properties comparable to those of conventionally processed alloys. However, the AM of NiTi SMAs remains underexplored due to the extreme complexity of the process, high melting point, and reactivity with oxygen. This study investigates the impact of AM processing on the shape memory properties of NiTi alloys using the Micro Wire and Arc Directed Energy Deposition (μ-WA-DED) technique in short circuit mode with a pioneering 0.3 mm pre-alloyed wire, focusing on increasing precision and control in the deposition process. The macroscopic morphology, microstructure, phase composition, phase-transformation temperatures, and mechanical properties of each deposited layer were analyzed. Results indicated austenite (B2) as the predominant phase, with retained martensite (B19′) and a reversible martensitic transformation (B2 ⇌ B19′) in the second layer. Mechanical characterization revealed variations in hardness (H) and elastic modulus (E) due to microstructural heterogeneity and composition. The first layer exhibited H = 3.8 GPa and E = 70 GPa, associated with the B2-NiTi phase, while higher values were obtained in the second layer, i.e., E = 100 GPa and H = 7 GPa. This study establishes for the first time the feasibility of NiTi alloy deposition with a 0.3 mm wire, setting a new standard for future research and applications in AM using μ-WA-DED. Full article
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<p>Schematic representation of the employed deposition strategy that was used to manufacture the NiTi walls by µ-WA-DED.</p>
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<p>(<b>a</b>) Schematic representation of the layer deposition with emphasis on the region analyzed by SEM, (<b>b</b>) cross-section along the longitudinal direction after metallographic preparation of the sample, (<b>c</b>) panoramic image of the printed NiTi part, and (<b>d</b>) 0.3 mm NiTi wire acquired from Fort Wayne Metals (Fort Wayne, IN, USA). BD: build direction.</p>
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<p>FESEM-BSE images of the microstructure in the (<b>a</b>,<b>b</b>) 1st and (<b>c</b>,<b>d</b>) 2nd layer with (<b>a</b>,<b>c</b>) low and (<b>b</b>,<b>d</b>) high magnification, highlighting the EDS analysis locations in the higher magnification images (i.e., (<b>b</b>,<b>d</b>)).</p>
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<p>FESEM-BSE high magnification image of the microstructure in the 2nd layer of the NiTi part.</p>
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<p>XRD patterns of the 1st and 2nd layers of the NiTi part.</p>
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<p>DSC curves of the NiTi part: (<b>a</b>) 1st layer; (<b>b</b>) 2nd layer and 2nd layer (cycled).</p>
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<p>(<b>a</b>) OM image of the cross-section of the printed NiTi part. (<b>b</b>) OM magnified image of the red-rectangle region highlighted in (<b>a</b>), showing the location of nanoindentation imprints. (<b>c</b>–<b>e</b>) FESEM-BSE images of the imprints localized in the two-dimensional array (<b>c</b>) and in the linear array (<b>d</b>,<b>e</b>).</p>
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<p>Extracted E and H values of the NiTi part as a function of the distance from the top side of the 2nd layer, denoted by a, to the bottom side of the 1st layer, denoted by f.</p>
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<p>E (<b>a</b>,<b>c</b>) and H (<b>b</b>,<b>d</b>) histograms of the NiTi part for the 1st (<b>a</b>,<b>b</b>) and 2nd (<b>c</b>,<b>d</b>) layer.</p>
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20 pages, 16271 KiB  
Article
Nonlinear Ultrasonic Characterization of Processing Defects in Wire Arc Additive Manufacturing 316L Stainless Steel
by Pengfei Wang, Jia Zeng, Dong Lou, Wenjian Zheng, Sanlong Zheng, Bingbing Chen and Zengliang Gao
Materials 2025, 18(4), 805; https://doi.org/10.3390/ma18040805 - 12 Feb 2025
Viewed by 391
Abstract
Wire Arc Additive Manufacturing (WAAM) 316L stainless steel unavoidably introduces defects such as porosity, oxide inclusions, and lack of fusion due to the inherent characteristics of the process. These defects can significantly affect the mechanical properties and service reliability of the material. This [...] Read more.
Wire Arc Additive Manufacturing (WAAM) 316L stainless steel unavoidably introduces defects such as porosity, oxide inclusions, and lack of fusion due to the inherent characteristics of the process. These defects can significantly affect the mechanical properties and service reliability of the material. This study focused on evaluating the defects in WAAM 316L stainless steel by nonlinear ultrasonic testing based on Lamb waves. The effects of FCAW (flux cored arc welding) parameters, including shielding gases (98% Ar + 2% O2 and 100% CO2) and welding speeds (20, 30, and 40 cm/min), on the columnar grain, porosity, and defect types were systematically analyzed. The formed specimens were then subjected to nonlinear ultrasonic testing, and the results showed that the ultrasonic nonlinear parameters exhibited high sensitivity to changes in porosity. This suggests that nonlinear ultrasonic testing can effectively assess processing defects in WAAM 316L stainless steel. The findings provide valuable insights for optimizing the WAAM process and improving the reliability of additive manufacturing components. Full article
(This article belongs to the Special Issue Advancements in Ultrasonic Testing for Metallurgical Materials)
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<p>The experimental platform.</p>
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<p>Schematic diagram of the multi-pass and multi-layer deposition directions.</p>
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<p>WAAM 316L plates. (<b>a</b>) V20; (<b>b</b>) V30; (<b>c</b>) V40. The letters A to F indicate the sampling positions for subsequent metallographic tests.</p>
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<p>Nonlinear ultrasonic testing system.</p>
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<p>Time-domain signal.</p>
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<p>Microstructure of V30 specimens. (<b>a</b>) Point C, the bottom; (<b>b</b>) point D, the middle; and (<b>c</b>) point E, the top.</p>
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<p>Microstructure at different welding speeds. (<b>a</b>) Point B, V20; (<b>b</b>) point E, V30; and (<b>c</b>) point F, V40.</p>
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<p>Metallography and element distribution of V20 specimen using SEM.</p>
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<p>Typical morphological characteristics of internal defects. (<b>a</b>) Lack-of-fusion; (<b>b</b>) micro-pore, V30; (<b>c</b>) oxide inclusion.</p>
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<p>The microstructures of selected WAAM 316L specimens. (<b>a</b>) Original micrograph; (<b>b</b>) Micrograph after binarization.</p>
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<p>Average porosity under different process parameters.</p>
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<p>Equivalent diameter under different process parameters. (<b>a</b>) V20; (<b>b</b>) V30; (<b>c</b>) V40; (<b>d</b>) V20(CO<sub>2</sub>).</p>
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<p>Relationship between equivalent diameter and <span class="html-italic">AR</span> under different process parameters. (<b>a</b>) V20; (<b>b</b>) V30; (<b>c</b>) V40; (<b>d</b>) V20(CO<sub>2</sub>).</p>
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<p>Relationship between equivalent diameter and <span class="html-italic">AR</span> under different process parameters. (<b>a</b>) V20; (<b>b</b>) V30; (<b>c</b>) V40; (<b>d</b>) V20(CO<sub>2</sub>).</p>
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<p>Relationship between <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>A</mi> </mrow> <mrow> <mn>1</mn> </mrow> <mrow> <mn>2</mn> </mrow> </msubsup> </mrow> </semantics></math> and <span class="html-italic">A</span><sub>2</sub> at different output levels.</p>
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<p>Relationship between nonlinear parameter and excitation frequency.</p>
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<p>Relationship between nonlinear parameter and propagation distance.</p>
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<p>Dimensions of the detection area.</p>
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<p>Frequency-domain signal.</p>
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<p>Relationship between defects characterization and normalized nonlinear parameter. (<b>a</b>) Porosity; (<b>b</b>) number of pores.</p>
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14 pages, 6418 KiB  
Article
Dynamic and Static Strength Analysis of 5056 Aluminum Alloy Fabricated by Wire-Arc Additive Manufacturing
by Alexey Evstifeev, Aydar Mavlyutov, Darya Volosevich, Marina Gushchina, Olga Klimova-Korsmik, Konstantin Nasonovskiy and Sofya Shabunina
Metals 2025, 15(2), 189; https://doi.org/10.3390/met15020189 - 12 Feb 2025
Viewed by 432
Abstract
This article presents the results of experimental studies on the dynamic and static strength of commercial aluminum alloy 5056 manufactured by wire-arc additive manufacturing (WAAM). The main objective is to evaluate the utilization potential of this technology for manufacturing parts for operation under [...] Read more.
This article presents the results of experimental studies on the dynamic and static strength of commercial aluminum alloy 5056 manufactured by wire-arc additive manufacturing (WAAM). The main objective is to evaluate the utilization potential of this technology for manufacturing parts for operation under shock loads. The dynamic tensile strength of the material was investigated with a modified Kolsky method, implemented by a split Hopkinson pressure bar. A comparative analysis of the strength characteristics of materials manufactured by WAAM and conventional cold-rolling methods was carried out using a structurally temporal approach with the incubation time criterion. The results showed that the aluminum alloy obtained by WAAM demonstrates comparable strength levels to that of cold-rolled material. The findings suggest that WAAM can be a competitive alternative for producing high-strength aluminum alloys for operation under shock loads. Full article
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<p>Scheme of a WAAM setup (<b>a</b>); the photo of AA5056_AM (<b>b</b>).</p>
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<p>The scheme of experimental tension test setup with SHPB.</p>
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<p>Backscattered electrons micrograph of (<b>a</b>) AA5056_IM and (<b>b</b>) AA5056_AM; (<b>c</b>) cross-sectional EBSD maps of AA5056_IM; (<b>d</b>) cross-sectional EBSD maps of AA5056_AM; 1–6 are the areas for EDS analysis.</p>
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<p>Fracture surface after tension test of AA5056_IM (<b>a</b>–<b>c</b>) and AA5056_AM (<b>d</b>–<b>f</b>). The Al6(Fe,Mn) particles are indicated by arrows on (<b>c</b>,<b>f</b>). The samples are marked (*) in <a href="#metals-15-00189-f007" class="html-fig">Figure 7</a>.</p>
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<p>Stress-time curves for AA5056_IM (<b>a</b>) and AA5056_AM (<b>b</b>), obtained under dynamic tension loads.</p>
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<p>Fracture surface after tension test of AA5056_IM (<b>a</b>–<b>c</b>) and AA5056_AM (<b>d</b>–<b>f</b>) on the split Hopkinson pressure bar. The Al6(Fe,Mn) particles are indicated by arrows. The samples are marked (**) in <a href="#metals-15-00189-f007" class="html-fig">Figure 7</a>.</p>
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<p>Experimental and calculated dependences of the maximum tensile strength on the stress rates ofAA5056_IM and AA5056_AM. The markers are experimental data, the curves are plotted according to criterion (1) considering the material parameters from <a href="#metals-15-00189-t004" class="html-table">Table 4</a>. Samples for surface fracture investigations after tension at static (*) and dynamic (**) modes.</p>
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16 pages, 5154 KiB  
Article
Microstructural Organization and Mechanical Properties of 5356 Aluminum Alloy Wire Arc Additive Manufacturing Under Low Heat Input Conditions
by Xiaogang Zuo, Zhimin Lv, Yuejie Wang, Xiaokang Chen and Wenjun Qi
Metals 2025, 15(2), 116; https://doi.org/10.3390/met15020116 - 25 Jan 2025
Viewed by 411
Abstract
This study examines the microstructure and mechanical properties of 5356 aluminum alloy under low heat input conditions during arc additive manufacturing, focusing on the challenges posed by excessive heat input, which hinders specimen formation and affects dimensional accuracy. The study analyzes the characteristics [...] Read more.
This study examines the microstructure and mechanical properties of 5356 aluminum alloy under low heat input conditions during arc additive manufacturing, focusing on the challenges posed by excessive heat input, which hinders specimen formation and affects dimensional accuracy. The study analyzes the characteristics of single-pass multilayer straight-walled specimens fabricated under varying low heat input conditions, along with evaluations of their mechanical properties, including their microstructure, microhardness, and tensile strength. This study demonstrates that as the heat input increases from 87.5 J/mm to 190.0 J/mm, the width of the vertical wall specimens increases significantly, whereas the change in single-layer height remains minimal. The specimen width increases from 5.22 mm to 8.87 mm, representing a change of 3.65 mm, while the single-layer height increases by only 0.16 mm. The microstructure primarily consists of the α(Al) matrix and the skeletal β(Al3Mg2) phase. As heat input increases, some of the β(Al3Mg2) phase dissolves, resulting in a decrease in its distribution density, a reduction in its quantity, and an increase in its size. The average hardness increases from 69.40 HV at 87.5 J/mm to 77.89 HV at 154.2 J/mm, before decreasing to 73.56 HV at 190.0 J/mm. As the heat input increases, the tensile strength and elongation of both horizontal and vertical specimens initially increase and then decrease. The tensile strength and elongation of the horizontal specimens are slightly greater than those of the vertical specimens. The microstructure and mechanical properties vary across different regions. In the upper region, the β(Al3Mg2) phase is uniformly distributed, with high density and small size. The fracture surface exhibits fine, uniform dimples, displaying the best microhardness and mechanical properties, with a tensile strength of 245.88 MPa. In the middle region, the distribution density of the β phase decreases, the size increases, and the dimples become slightly coarser. Consequently, the microhardness and mechanical properties decline. At the bottom, due to the higher cooling rates, the β phase does not dissolve significantly. The distribution density is high, the dimples are large and uneven, and the microhardness and mechanical properties are the lowest, with a tensile strength of 236.00 MPa. Full article
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<p>Schematic of arc additive manufacturing equipment.</p>
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<p>(<b>a</b>) The reciprocating stacking path; (<b>b</b>) the molding effect on the substrate with and without preheating at 90 °C.</p>
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<p>(<b>a</b>) A schematic illustration of the sampling positions; (<b>b</b>) the dimensions of the tensile specimens.</p>
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<p>Forming effects of straight-walled specimens under different low heat input levels: (<b>a</b>) 87.5 J/mm; (<b>b</b>) 120.0 J/mm; (<b>c</b>) 154.2 J/mm; (<b>d</b>) 190.0 J/mm.</p>
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<p>Variation in width and single-layer height of straight-walled specimens.</p>
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<p>XRD spectrum of 5356 aluminum alloy WAAM specimens.</p>
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<p>Microstructural morphology at different positions: (<b>a</b>) top OM image; (<b>b</b>) middle OM image; and (<b>c</b>) bottom OM image.</p>
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<p>Microstructural morphology at different low heat input levels: (<b>a</b>) 87.5 J/mm; (<b>b</b>) 120.0 J/mm; (<b>c</b>) 154.2 J/mm; and (<b>d</b>) 190.0 J/mm.</p>
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<p>EDS analysis of 5356 aluminum alloy WAAM specimens: (<b>a</b>) point scan EDS; (<b>b</b>) line scan EDS.</p>
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<p>The microhardness of 5356 aluminum alloy WAAM specimens at different low heat input levels. (<b>a</b>) The hardness of the sample from the substrate to the top under different heat inputs. (<b>b</b>) The average hardness under different heat inputs.</p>
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<p>Tensile properties at different positions.</p>
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<p>Mechanical properties of 5356 aluminum alloy WAAM specimens at different low heat input levels: (<b>a</b>) tensile properties; (<b>b</b>) elongation.</p>
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<p>Tensile fracture morphology of 5356 aluminum alloy WAAM samples at different positions: (<b>a</b>) upper fracture SEM image, (<b>b</b>) middle fracture SEM image, (<b>c</b>) lower fracture SEM image, and (<b>d</b>) vertical sample fracture SEM image.</p>
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17 pages, 20460 KiB  
Article
Integration of Arc and Microstructural Analysis for Anomaly Detection in Walls Manufactured by GMA-Based WAAM
by Lucas J. E. B. Santos, Joyce I. V. Souto, Igo J. S. Azevedo, Walman B. Castro, Jefferson S. Lima, João M. P. Q. Delgado, Renato A. C. Santana, Ricardo S. Gomez, André L. D. Bezerra and Antonio G. B. Lima
Metals 2025, 15(2), 110; https://doi.org/10.3390/met15020110 - 24 Jan 2025
Viewed by 524
Abstract
Wire Arc Additive Manufacturing (WAAM) is a process for fabricating metal parts known for its high productivity and material flexibility. However, defects such as overheating, residual stresses, distortions, porosity, and a non-homogeneous microstructure limit its commercial applications. Therefore, the present study aims to [...] Read more.
Wire Arc Additive Manufacturing (WAAM) is a process for fabricating metal parts known for its high productivity and material flexibility. However, defects such as overheating, residual stresses, distortions, porosity, and a non-homogeneous microstructure limit its commercial applications. Therefore, the present study aims to analyze the correlation between electrical sensing anomalies in the Gas Metal Arc (GMA) during WAAM and the occurrence of microscopic defects caused by external contamination. To achieve this, experiments were conducted to fabricate walls using WAAM with controlled contaminant introduction. Simultaneously, electrical arc data, specifically voltage and current, were segmented and acquired during the wall deposition process. Metallographic analysis confirmed the presence of microscopic defects or changes in the solidification patterns in regions with contaminant inclusion, distinguishing them from other areas of the analyzed samples. Similarly, the contaminations were proven to cause anomalies in attributes associated with the electrical arc. Therefore, this approach confirms the criticality of electrical arc monitoring in WAAM, as it demonstrates that anomalies in the electrical arc could lead to microstructural consequences. Full article
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<p>(<b>a</b>) Schematic diagram of contaminant insertion during layer deposition by MADA, according to strategies (<b>b</b>) P1 and (<b>c</b>) P2. The red dots indicate the exact locations of contaminant introduction.</p>
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<p>Fabricated walls: (<b>a</b>) W2, (<b>b</b>) W3, (<b>c</b>) W4, (<b>d</b>) W5, (<b>e</b>) W6, (<b>f</b>) W7, and (<b>g</b>) W1.</p>
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<p>Fabricated walls: (<b>a</b>) W2, (<b>b</b>) W3, (<b>c</b>) W4, (<b>d</b>) W5, (<b>e</b>) W6, (<b>f</b>) W7, and (<b>g</b>) W1.</p>
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<p>Microstructure of wall W2 at 50× magnification. The white circles indicate noticeable microstructural defects.</p>
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<p>Microstructure of wall W3 at 50× magnification. The white circle indicates noticeable microstructural defects.</p>
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<p>Microstructure of wall W4 at 50× magnification. The white circles indicate noticeable microstructural defects.</p>
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<p>Microstructure of wall W5 at 50× magnification.</p>
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<p>Microstructure of wall W6 at 50× magnification.</p>
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<p>Microstructure of wall W7 at 50× magnification.</p>
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<p>Examples of the features extracted from the electrical arc data: (<b>a</b>) standard deviation values, (<b>b</b>) minimum values, (<b>c</b>) number of peaks, and (<b>d</b>) average values. The dotted red squares indicate regions of the oscillogram where some type of electric arc anomaly occurred, marked by the acronyms ONC, AC, and OFC.</p>
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<p>Correlation matrix between electric arc features.</p>
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18 pages, 5510 KiB  
Article
Towards an Automated Design Evaluation Method for Wire Arc Additive Manufacturing
by Johannes Pusicha, Henrik Stromberg, Markus Quanz and Armin Lohrengel
Appl. Sci. 2025, 15(2), 938; https://doi.org/10.3390/app15020938 - 18 Jan 2025
Viewed by 753
Abstract
Freedom of design and the cost-effective production of structural parts have led to much research interest in Wire Arc Additive Manufacturing (WAAM). Nevertheless, WAAM is subject to design constraints and fundamentally differs from other additive manufacturing processes. Consequently, design guidelines and supporting design [...] Read more.
Freedom of design and the cost-effective production of structural parts have led to much research interest in Wire Arc Additive Manufacturing (WAAM). Nevertheless, WAAM is subject to design constraints and fundamentally differs from other additive manufacturing processes. Consequently, design guidelines and supporting design evaluation tools adapted to WAAM are needed. One geometric approach to design evaluation is the use of a three-dimensional medial axis transformation (3D-MAT) to derive local geometry indicators. Previous works define the thickness and radius indicators. In this work, the angle between opposing faces and a mass gradient indicator are added. To apply the literature design rules regarding wall thickness, clearance, bead angle, and edge radius to specific geometry regions, features are classified by the indicators. Following a literature suggestion, wall and corner regions are differentiated by the angle indicator. An angle of 65° is identified as an effective separation limit. Additionally, the analogy of Heuvers’ spheres to the MAT helps estimate a limit of kH1kH+1 for the mass gradient (kH: Heuvers’ factor). Finally, tests on example parts demonstrate the method’s effectiveness in verifying compliance to the specified rules. With a numerical complexity of O(n2), this method is more efficient than finite element analyses, providing early feedback in the design process. Full article
(This article belongs to the Section Mechanical Engineering)
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<p>Example for Heuvers’ circles with different diameters <span class="html-italic">D</span> and <span class="html-italic">d</span>.</p>
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<p>Medial axis and medial surface as dual representation of a geometry delivering its local symmetry axis or plane. The medial axis and the medial surface are defined by the set of all midpoints of maximally inscribed circles and spheres, respectively.</p>
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<p>Dimensions of the 3D-MAT: <math display="inline"><semantics> <mi mathvariant="bold">p</mi> </semantics></math>, <math display="inline"><semantics> <mi mathvariant="bold">b</mi> </semantics></math>: tangent points; <math display="inline"><semantics> <msub> <mi mathvariant="bold">n</mi> <mi>p</mi> </msub> </semantics></math>, <math display="inline"><semantics> <msub> <mi mathvariant="bold">n</mi> <mi>b</mi> </msub> </semantics></math>: normal vectors; <math display="inline"><semantics> <mi>α</mi> </semantics></math>: wall angle; <span class="html-italic">s</span>: secant; <math display="inline"><semantics> <msub> <mi>g</mi> <mi>r</mi> </msub> </semantics></math>: 2D gradient.</p>
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<p>Different applications of Heuvers’ sphere.</p>
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<p>Comparison of various outer and inner angles and the secant used (red). Sections with an enclosed angle of <math display="inline"><semantics> <mrow> <mn>0</mn> <mo>≤</mo> <mi>α</mi> <mo>≤</mo> <msup> <mn>65</mn> <mo>°</mo> </msup> </mrow> </semantics></math> can be considered as tapered wall.</p>
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<p>Overview of the implemented software architecture.</p>
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<p>Example bar part to verify our implementation. Design flaws on the left-hand side, and corresponding corrections on the right-hand side. All dimensions are indicated in millimeters.</p>
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<p>Approximations of the medial surfaces of the example part. The center points of the inscribed spheres are color-coded by their radius in millimeters.</p>
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<p>Evaluation results on the example part. For each feature, non-manufacturable faces are highlighted with a color scale from yellow to red with ascending constraint violation.</p>
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<p>Some testing results on three benchmark geometries. Note that some color scales and feature limits have been adjusted to better represent the recognition of the feature. In general, the features are measured correctly, despite the above described classification issues with thin walled regions.</p>
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<p>Some testing results on three benchmark geometries. Note that some color scales and feature limits have been adjusted to better represent the recognition of the feature. In general, the features are measured correctly, despite the above described classification issues with thin walled regions.</p>
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18 pages, 40226 KiB  
Article
The Effect of Post-Deposition Heat Treatment on the Microstructure, Texture, and Mechanical Properties of Inconel 718 Produced by Hybrid Wire-Arc Additive Manufacturing with Inter-Pass Forging
by Dmitrii Panov, Gleb Permyakov, Stanislav Naumov, Vladimir Mirontsov, Egor Kudryavtsev, Liying Sun, Alexander Aksenov, Nikita Stepanov, Dmitriy Trushnikov and Gennady Salishchev
Metals 2025, 15(1), 78; https://doi.org/10.3390/met15010078 - 17 Jan 2025
Viewed by 827
Abstract
The microstructure, texture, and mechanical properties of Inconel 718 fabricated via hybrid wire-arc additive manufacturing (WAAM) with inter-pass forging, and the subsequent modified post-deposition heat treatment (PDHT), were investigated. The modified PDHT included homogenization at 1185 °C and double ageing at 720 °C, [...] Read more.
The microstructure, texture, and mechanical properties of Inconel 718 fabricated via hybrid wire-arc additive manufacturing (WAAM) with inter-pass forging, and the subsequent modified post-deposition heat treatment (PDHT), were investigated. The modified PDHT included homogenization at 1185 °C and double ageing at 720 °C, with furnace-cooling to 620 °C; this process was first used for Inconel 718 obtained via WAAM and inter-pass forging. In the as-printed material, two characteristic zones were distinguished, as follows: (i) columnar grains with a preferable <100> orientation and (ii) fine grains with a random crystallographic orientation. The development of static recrystallization induced via inter-pass forging and further heating during the deposition of the next (upper) layer provoked the formation of the fine-grained zone. In the as-printed material, particles of (Nb,Ti)C and TiN, and precipitates of a Nb-rich Laves phase that caused premature cracking and failure during mechanical testing, were detected. In the PDHT material, two zones were found, as follows: (i) a zone with coarse uniaxial grains and (ii) a zone with a gradient grain size distribution. PDHT resulted in the precipitation of γ″ nanoparticles in the γ-Ni matrix and the dissolution of the brittle Laves phase. Therefore, significant hardening and strengthening, as well as increases in ductility and impact toughness, occurred. Full article
(This article belongs to the Section Additive Manufacturing)
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<p>(<b>a</b>) A functional scheme of the hybrid CMT-WAAM forging setup (1, current welding source TPS 5000 CMT; 2, remote control setup RCU 5000i; 3, cooling setup FK4000-R; 4, wire-feeding mechanism VR7000-CMT; 5, wire buffer CMT; 6, welding torch Robacta Drive CMT; 7, pneumatic hammer; 8, two-axis table; 9, machining center column; 10, control panel). (<b>b</b>) Hybrid Cold Metal Transfer (CMT) WAAM and forging setup and (<b>c</b>) as-printed Inconel 718 with inter-pass forging paths (A, 1st pass; B, 2nd pass; C, 3rd pass).</p>
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<p>The schemes of the deposition strategy with (<b>a</b>) 45° and (<b>b</b>) −45° oscillations.</p>
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<p>The modified PDHT regime of the as-printed material adapted from [<a href="#B30-metals-15-00078" class="html-bibr">30</a>,<a href="#B49-metals-15-00078" class="html-bibr">49</a>,<a href="#B50-metals-15-00078" class="html-bibr">50</a>].</p>
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<p>(<b>a</b>) A scheme of specimen cutting and sketches of specimens for (<b>b</b>) impact toughness (adapted from ISO 148-1 [<a href="#B53-metals-15-00078" class="html-bibr">53</a>]) and (<b>c</b>) tensile testing (adapted from ISO 6892 [<a href="#B54-metals-15-00078" class="html-bibr">54</a>]).</p>
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<p>XRD patterns of as-printed and PDHT Inconel 718.</p>
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<p>EBSD analysis of (<b>a</b>,<b>b</b>) as-printed and (<b>c</b>,<b>d</b>) PDHT Inconel 718 materials: (<b>a</b>,<b>c</b>) inverse pole figure (IPF) maps and (<b>b</b>,<b>d</b>) kernel average misorientation (KAM) maps. (<b>a<sub>1</sub></b>) IPF and (<b>a<sub>2</sub></b>) phase (red color represents austenite (γ)) maps with higher magnification inserted in (<b>a</b>). KAM maps in (<b>b</b>,<b>d</b>) were collected from cropped areas in (<b>a</b>,<b>c</b>), respectively.</p>
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<p>SEM-BSE observations of welding wire 3D print AM 718: (<b>a</b>) longitudinal section; (<b>b</b>) transverse section. Corresponding results of EDS-analysis are presented in (<b>a</b>,<b>b</b>).</p>
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<p>SEM-BSE observations of as-printed Inconel 718: (<b>a</b>) interlayer boundary, (<b>b</b>) zone 1, (<b>c</b>) zone 2, and (<b>d</b>) element distribution maps generated via EDS-analysis from the selected region in zone 1.</p>
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<p>SEM-BSE observations of PDHT Inconel 718: (<b>a</b>) interlayer boundary, (<b>b</b>) zone 1, (<b>c</b>) zone 2, and (<b>d</b>) element distribution maps generated via EDS-analysis from the selected region in zone 1.</p>
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<p>The volume fractions of the Laves phase and (Nb,Ti)C carbides in the welding wire, as-printed wall, and PDHT Inconel 718.</p>
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<p>TEM observations of PDHT Inconel 718: (<b>a</b>) bright-field image; (<b>b</b>) dark-field image in the <math display="inline"><semantics> <mrow> <mfenced separators="|"> <mrow> <mn>0</mn> <mover accent="true"> <mrow> <mn>1</mn> </mrow> <mo>¯</mo> </mover> <mn>1</mn> </mrow> </mfenced> </mrow> </semantics></math>γ″ reflection; (<b>c</b>) selected area electron diffraction (SAED) patterns of the <math display="inline"><semantics> <mrow> <mfenced open="&#x2329;" close="&#x232A;" separators="|"> <mrow> <mn>001</mn> </mrow> </mfenced> </mrow> </semantics></math> γ-Ni zone axis from the field indicated by the dotted circle in (<b>a</b>).</p>
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<p>(<b>a</b>) Microhardness distribution and (<b>b</b>) engineering stress–strain curves of as-printed and PDHT Inconel 718.</p>
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<p>Fracture overview and microphotographs of tensile specimens of (<b>a</b>–<b>c</b>) as-printed and (<b>d</b>–<b>f</b>) PDHT Inconel 718.</p>
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<p>Fracture profiles of tensile specimens of (<b>a</b>) as-printed and (<b>b</b>) PDHT Inconel 718.</p>
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<p>Fracture overview and microphotographs of impact toughness specimens of (<b>a</b>–<b>c</b>) as-printed and (<b>d</b>–<b>f</b>) PDHT Inconel 718.</p>
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<p>Yield strength (YS) and ultimate elongation (UE) combination of Inconel 718 obtained using CMT/Plasma-WAAM processing adapted from [<a href="#B30-metals-15-00078" class="html-bibr">30</a>,<a href="#B31-metals-15-00078" class="html-bibr">31</a>,<a href="#B33-metals-15-00078" class="html-bibr">33</a>,<a href="#B39-metals-15-00078" class="html-bibr">39</a>,<a href="#B77-metals-15-00078" class="html-bibr">77</a>,<a href="#B78-metals-15-00078" class="html-bibr">78</a>].</p>
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15 pages, 5027 KiB  
Article
Hybridization in Metal Wire Additive Manufacturing: A Case Study of an Impeller
by Shahu R. Karade, Siddhartha Siddhartha, Neel Kamal Gupta, Ganesan G, K. P. Karunakaran and Henning Zeidler
Metals 2025, 15(1), 71; https://doi.org/10.3390/met15010071 - 15 Jan 2025
Viewed by 733
Abstract
Additive manufacturing (AM) has evolved to enable the direct production of functional components through the hybridization of additive and subtractive processes. In metal wire AM, hybridization is key, encompassing process integration (addition/subtraction), energy source combinations (arc/laser), kinematic options (3/4/5 axis), and slicing techniques [...] Read more.
Additive manufacturing (AM) has evolved to enable the direct production of functional components through the hybridization of additive and subtractive processes. In metal wire AM, hybridization is key, encompassing process integration (addition/subtraction), energy source combinations (arc/laser), kinematic options (3/4/5 axis), and slicing techniques (planar/conformal). This paper focuses on these hybridization methods, with a unified system designed for single-machine setups, improving efficiency and accuracy. This study presents a detailed exploration of these hybridization levels through the fabrication of a complex 5-axis geometry—an impeller. The impeller was manufactured with hybridization using various levels and subsequently compared with manufacturing processes like additive manufacturing with interlayer machining and traditional machining methods. The hybrid approach significantly reduced the manufacturing time for the selected impeller geometry from 3536 min to 792 min (saving 77.6% manufacturing time) and minimized material waste to 9.3%, compared with 74.07% in traditional machining. This demonstrates a more efficient, precise, and cost-effective method to optimize metal wire AM for producing complex metal components, advancing capabilities and applications. Full article
(This article belongs to the Special Issue Additive Manufacturing of Metallic Materials)
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Figure 1

Figure 1
<p>Illustration of component with planar and conformal slicing: (<b>a</b>) Actual geometry. (<b>b</b>) Planar slicing—front view. (<b>c</b>) Planar slicing—isometric view. (<b>d</b>) Conformal slicing—front view. (<b>e</b>) Planar slicing—isometric View.</p>
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<p>Illustration of slicing strategies: (<b>a</b>) Single slicing. (<b>b</b>) Double slicing.</p>
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<p>Setup for deposition.</p>
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<p>Operations flow chart for planar and conformal strategies.</p>
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<p>Double slicing of impeller: (<b>a</b>) Front view. (<b>b</b>) Top view.</p>
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<p>Conformal slicing of impeller: (<b>a</b>) Planar slicing of hub. (<b>b</b>) Conformal slicing of blades. (<b>c</b>) Conformal toolpath growth of all blades at mid of both surfaces.</p>
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<p>Manufacturing stages of conformal impeller: (<b>a</b>) CAD model of hub. (<b>b</b>) CAD of blades over hub. (<b>c</b>) Near net hub deposition. (<b>d</b>) Machined hub. (<b>e</b>) Intermediate layer of blades. (<b>f</b>) Intermittent machining of blade surface for geometry accuracy.</p>
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<p>Stress–strain curve for interlayer machining and without interlayer machining.</p>
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<p>(<b>a</b>) MIG torch with planar 5-axis deposition. (<b>b</b>) Laser with conformal 5-axis deposition.</p>
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<p>Impeller manufactured in both cases: (<b>a</b>) Near net after planar strategy. (<b>b</b>) Finished impeller after planar deposition. (<b>c</b>) Near net after conformal strategy. (<b>d</b>) Finished impeller after conformal deposition.</p>
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