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Laser Additive Manufacturing: Design, Materials, Processes and Applications, 2nd Edition

A special issue of Micromachines (ISSN 2072-666X). This special issue belongs to the section "D3: 3D Printing and Additive Manufacturing".

Deadline for manuscript submissions: closed (31 December 2023) | Viewed by 17021

Special Issue Editors


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Guest Editor
Advanced Manufacturing Research Center, Gemological Institute, China University of Geosciences, Wuhan 430074, China
Interests: additive manufacturing; laser advanced manufacturing; laser-matter interaction; numerical simulation; in situ characterization; microstructures; mechanical properties
Special Issues, Collections and Topics in MDPI journals
Department of Mechanical Engineering, Ningbo University, Ningbo 315211, China
Interests: additive manufacturing; selective laser melting; crystal plasticity finite element; dynamic mechanical properties; titanium alloy; metal matrix composites
Special Issues, Collections and Topics in MDPI journals
Shanghai Engineering Technology Research Center of Near-Net-Shape Forming for Metallic Materials, Shanghai Spaceflight Precision Machinery Institute, Shanghai 201600, China
Interests: additive manufacturing; selective laser melting; wire arc additive manufacturing; structure design; magnesium alloy
TSC Laser Technology Development (Beijing) Co., Ltd., Beijing 100076, China
Interests: additive manufacturing; selective laser melting; 3D printing; microstructures; mechanical properties

Special Issue Information

Dear Colleagues,

Following on from the success of the initial Special Issue on laser-based additive manufacturing (LAM), this second volume continues our exploration of the ever-advancing progress of the design, materials, processes and applications of LAM. LAM is a revolutionary advanced digital manufacturing and key strategic technology for technological innovation and industrial sustainability. This technology unlocks the constraints of traditional manufacturing and meets the needs of complex geometry fabrication and high-performance part fabrication. A deeper understanding of the design, materials, processes, structures, properties and applications of this technology is needed to produce novel functional devices, as well as defect-free structurally sound and reliable AM parts.

This Special Issue of Micromachines entitled "Laser Additive Manufacturing: Design, Materials, Processes and Applications, Volume II" aims to cover all the possible topics in this field, including macro- to micro-scale additive manufacturing with lasers, including structure design, fabrication, modeling and simulation; in situ characterization of additive manufacturing processes; and ex situ material characterization and performances, with an overview of various applications in aerospace, biomedicine, optics, transportation and energy, etc.

It is our pleasure to invite you to contribute original articles, comprehensive reviews and letters/opinions to this Special Issue.

Prof. Dr. Jie Yin
Dr. Yang Liu
Dr. Linda Ke
Dr. Kai Guan
Guest Editors

Manuscript Submission Information

Manuscripts should be submitted online at www.mdpi.com by registering and logging in to this website. Once you are registered, click here to go to the submission form. Manuscripts can be submitted until the deadline. All submissions that pass pre-check are peer-reviewed. Accepted papers will be published continuously in the journal (as soon as accepted) and will be listed together on the special issue website. Research articles, review articles as well as short communications are invited. For planned papers, a title and short abstract (about 100 words) can be sent to the Editorial Office for announcement on this website.

Submitted manuscripts should not have been published previously, nor be under consideration for publication elsewhere (except conference proceedings papers). All manuscripts are thoroughly refereed through a single-blind peer-review process. A guide for authors and other relevant information for submission of manuscripts is available on the Instructions for Authors page. Micromachines is an international peer-reviewed open access monthly journal published by MDPI.

Please visit the Instructions for Authors page before submitting a manuscript. The Article Processing Charge (APC) for publication in this open access journal is 2600 CHF (Swiss Francs). Submitted papers should be well formatted and use good English. Authors may use MDPI's English editing service prior to publication or during author revisions.

Keywords

  • additive manufacturing
  • 3D printing
  • laser powder bed fusion
  • laser-directed energy deposition
  • laser advanced manufacturing
  • design and modeling
  • materials
  • processes
  • characterization
  • mechanical and functional properties
  • applications

Related Special Issue

Published Papers (12 papers)

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Editorial

Jump to: Research, Review

6 pages, 982 KiB  
Editorial
Editorial for the Special Issue on Laser Additive Manufacturing: Design, Materials, Processes, and Applications, 2nd Edition
by Jie Yin, Yang Liu, Linda Ke and Kai Guan
Micromachines 2024, 15(6), 787; https://doi.org/10.3390/mi15060787 - 15 Jun 2024
Viewed by 305
Abstract
Laser-based additive manufacturing (LAM) represents one of the most forward-thinking transformations in how we conceive, design, and bring to life engineered solutions [...] Full article
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<p>Topics covered in the Special Issue titled “Laser Additive Manufacturing: Design, Materials, Processes, and Applications, 2nd Edition”.</p>
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Research

Jump to: Editorial, Review

17 pages, 11474 KiB  
Article
Microstructure, Tensile Properties, and Fracture Toughness of an In Situ Rolling Hybrid with Wire Arc Additive Manufacturing AerMet100 Steel
by Lei Lei, Linda Ke, Yibo Xiong, Siyu Liu, Lei Du, Mengfan Chen, Meili Xiao, Yanfei Fu, Fei Yao, Fan Yang, Kun Wang and Baohui Li
Micromachines 2024, 15(4), 494; https://doi.org/10.3390/mi15040494 - 3 Apr 2024
Viewed by 741
Abstract
As a type of ultra-high strength steel, AerMet100 steel is used in the aerospace and military industries. Due to the fact that AerMet100 steel is difficult to machine, people have been exploring the process of additive manufacturing to fabricate AerMet100 steel. In this [...] Read more.
As a type of ultra-high strength steel, AerMet100 steel is used in the aerospace and military industries. Due to the fact that AerMet100 steel is difficult to machine, people have been exploring the process of additive manufacturing to fabricate AerMet100 steel. In this study, AerMet100 steel was produced using an in situ rolling hybrid with wire arc additive manufacturing. Microstructure, tensile properties, and fracture toughness of as-deposited and heat-treated AerMet100 steel were evaluated in different directions. The results reveal that the manufacturing process leads to grain fragmentation and obvious microstructural refinement of the AerMet100 steel, and weakens the anisotropy of the mechanical properties. After heat treatment, the microstructure of the AerMet100 steel is mainly composed of lath martensite and reversed austenite. Alloy carbides are precipitated within the martensitic matrix, and a high density of dislocations is the primary strengthening mechanism. The existence of film-like austenite among the martensite matrix enhances the toughness of AerMet100 steel, which coordinates stress distribution and restrains crack propagation, resulting in an excellent balance between strength and toughness. The AerMet100 steel with in situ rolling is isotropy and achieves the following values: an average ultimate strength of 1747.7 ± 16.3 MPa, yield strength of 1615 ± 40.6 MPa, elongation of 8.3 ± 0.2% in deposition direction, and corresponding values in the building direction are 1821.3 ± 22.1 MPa, 1624 ± 84.5 MPa, and 7.6 ± 1.7%, and the KIC value up to 70.6 MPa/m0.5. Full article
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<p>In situ rolling hybrid wire arc additive manufacturing AerMet100 steel process and defining direction.</p>
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<p>(<b>a</b>) Straight wall of AerMet100 steel produced using in situ rolling hybrid wire arc additive manufacturing; (<b>b</b>) sampling diagrams in different directions; (<b>c</b>) the size of the fracture toughness sample.</p>
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<p>Microstructure of as-deposited AerMet100 steel fabricated using WAAM hybrid with in situ rolling: microstructure morphology in planes perpendicular to (<b>a</b>,<b>b</b>) <span class="html-italic">Y</span>-axis; (<b>c</b>,<b>d</b>) <span class="html-italic">X</span>-axis and (<b>e</b>,<b>f</b>) <span class="html-italic">Z</span>-axis.</p>
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<p>Microstructure morphology of AerMet100 after heat treatment produced using an in situ rolling hybrid WAAM process: microstructure morphology in planes perpendicular to the (<b>a</b>,<b>b</b>) <span class="html-italic">Y</span>-axis; (<b>c</b>,<b>d</b>) <span class="html-italic">X</span>-axis and (<b>e</b>,<b>f</b>) <span class="html-italic">Z</span>-axis.</p>
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<p>Tensile results of the as-deposited AerMet100 specimens in different directions: (<b>a</b>) stress–strain curves and (<b>b</b>) the corresponding ultimate tensile strength, yield strength, and elongation.</p>
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<p>Tensile results of the heat-treated AerMet100 specimens in different directions: (<b>a</b>) stress–strain curves and (<b>b</b>) the corresponding ultimate tensile strength, yield strength, and elongation.</p>
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<p>Tensile fracture morphology of AerMet100 steel in different directions: (<b>a</b>) as-deposited specimen in DD; (<b>b</b>) as-deposited specimen in BD; (<b>c</b>) heat-treated specimen in DD; (<b>d</b>) heat-treated specimen in BD.</p>
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<p>Fracture surface morphology of the plain–strain fracture toughness specimen: (<b>a</b>) macrostructure in DD; (<b>b</b>) macrostructure in BD; (<b>c</b>) microstructure in DD; (<b>d</b>) microstructure in BD.</p>
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<p>A summary chart of AerMet100 mechanical properties.</p>
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<p>(<b>a</b>) Martensite lath in heat-treated AerMet100 steel; (<b>b</b>) austenite reconstruction of the microstructure in (<b>a</b>); (<b>c</b>) inverse pole figure of (<b>a</b>).</p>
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<p>TEM photographs of heat-treated AerMet100 steel: (<b>a</b>) the lath martensite with high-density dislocation in it, (<b>b</b>) the carbide precipitation.</p>
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<p>Crack expansion path: (<b>a</b>) in the deposition direction; (<b>b</b>) in the building direction.</p>
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<p>Film-like austenite distribution at the boundary of lath martensite in heat-treated AerMet100 steel: (<b>a</b>) EBSD phase composition characterization; (<b>b</b>) TEM morphology.</p>
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17 pages, 9122 KiB  
Article
Design and Optimization of Thin-Walled Main Support Structure for Space Camera Based on Additive Manufacturing
by Jiahao Peng, Shijie Liu, Dong Wang, Anpeng Xu, Xin Huang, Tianqi Ma, Jing Wang and Hang Li
Micromachines 2024, 15(2), 211; https://doi.org/10.3390/mi15020211 - 30 Jan 2024
Viewed by 832
Abstract
In order to solve the design requirements of high stiffness and lightweight for the primary support structure of a wide-field auroral imager, we propose a solution for designing and optimizing a large-scale complex thin-walled structure using additive manufacturing. Firstly, we devise an integrated [...] Read more.
In order to solve the design requirements of high stiffness and lightweight for the primary support structure of a wide-field auroral imager, we propose a solution for designing and optimizing a large-scale complex thin-walled structure using additive manufacturing. Firstly, we devise an integrated thin-walled structure and test material for the main support. Secondly, shape optimization is achieved via the optimization of the lateral slope angle of the primary support based on Timoshenko cantilever beam theory. Additionally, an active fitting optimization algorithm is proposed for the purpose of refining the wall thickness of the thin-walled structure. Then, we determine the structural design of the main support. This primary support is manufactured via selective laser melting (SLM). Following processing, the structure size is 538 mm × 400 mm × 384 mm, and the mass is 7.78 kg. Finally, frequency scanning experiments indicate that, in the horizontal direction, there is a natural frequency of 105.97 Hz with an error rate of approximately 3% compared to finite element analysis results. This research confirms that our large-scale complex, thin-walled main support structure design meets all design requirements. Full article
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<p>Sketch of the camera structure.</p>
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<p>Traditional structural form of main support.</p>
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<p>Preliminary structural sketch.</p>
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<p>Main support optimization variables.</p>
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<p>Optimization results of the lateral slope angle.</p>
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<p>Structural reinforcement of the main support.</p>
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<p>Finite element model.</p>
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<p>Changes in the fitted curves during the optimization process.</p>
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<p>Frequency residuals in the convergence process.</p>
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<p>Horizontal modal vibration pattern of space camera. (<b>a</b>) Y direction natural frequency, (<b>b</b>) X direction natural frequency.</p>
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<p>The BLT-S615 multi-metal 3D printing system.</p>
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<p>Sweep frequency vibration test site.</p>
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<p>X-direction sweep test results.</p>
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0 pages, 5254 KiB  
Article
Dynamic Compressive Properties and Failure Mechanism of the Laser Powder Bed Fusion of Submicro-LaB6 Reinforced Ti-Based Composites
by Xianghui Li and Yang Liu
Micromachines 2023, 14(12), 2237; https://doi.org/10.3390/mi14122237 - 13 Dec 2023
Viewed by 802
Abstract
In this study, lanthanum hexaboride (LaB6) particle-reinforced titanium matrix composites (PRTMCs, TC4/LaB6) were successfully manufactured using the laser powder bed fusion (LPBF) process. Thereafter, the effect of the mass fraction of LaB6 on the microstructure and the dynamic [...] Read more.
In this study, lanthanum hexaboride (LaB6) particle-reinforced titanium matrix composites (PRTMCs, TC4/LaB6) were successfully manufactured using the laser powder bed fusion (LPBF) process. Thereafter, the effect of the mass fraction of LaB6 on the microstructure and the dynamic compressive properties was investigated. The results show that the addition of LaB6 leads to significant grain refinement. Moreover, the general trend of grain size reveals a concave bend as the fraction increases from 0.2% to 1.0%. Furthermore, the texture intensity of prior β grains and α grains was found to be weakened in the composites. It was also observed that the TC4/LaB6 have higher quasi-static and dynamic compressive strengths but lower fracture strain when compared with the as-built TC4. The sample with 0.5 wt.% LaB6 was found to have the best strength–toughness synergy among the three groups of composites due to having the smallest grain size. Furthermore, the fracture mode of TC4/LaB6 was found to change from the fracture under the combined action of brittle and ductility to the cleavage fracture. This study was able to provide a theoretical basis for an in-depth understanding of the compressive properties of additive manufacturing of PRTMCs under high-speed loading conditions. Full article
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<p>SEM images of raw powders: (<b>a</b>) gas-atomized spherical TC4 powder, (<b>b</b>) irregular LaB<sub>6</sub> nanoparticle, (<b>c</b>) composite powder after ball milling, and (<b>d</b>) higher magnification image showing the nanoparticles adhering to the surface of Ti particles.</p>
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<p>SEM images of microstructure of (<b>a</b>) TMC0, (<b>b</b>) TMC1, (<b>c</b>) TMC2, and (<b>d</b>) TMC3.</p>
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<p>Bright-field TEM images of LPBF samples and corresponding selected area electron diffraction patterns: (<b>a</b>–<b>c</b>) TMC0, (<b>d</b>–<b>f</b>) TMC3.</p>
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<p>(<b>a</b>,<b>b</b>) High-resolution transmission electron microscopy (HRTEM) images of the nano-sized particle of TMC3.</p>
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<p>EBSD inverse pole figures (IPF), pole figures (PF), and the average grain size of LPBF samples: (<b>a</b>,<b>e</b>) TMC0, (<b>b</b>,<b>f</b>) TMC1, (<b>c</b>,<b>g</b>) TMC2, (<b>d</b>,<b>h</b>) TMC3, and (<b>i</b>) average grain size.</p>
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<p>Quasi-static compressive properties of TC4/LaB6 with different mass fractions: (<b>a</b>) engineering stress–strain curves; (<b>b</b>) compressive 0.2% proof stress and failure strain.</p>
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<p>Dynamic compressive properties of LPBF of TC4/LaB6 composites with different mass fractions at different strain rates (1800/s, 2500/s and 3000/s): (<b>a</b>,<b>c</b>,<b>e</b>) engineering stress–strain curves; (<b>b</b>,<b>d</b>,<b>f</b>) ultimate compressive strength and failure strain.</p>
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<p>Ultimate compressive strength for strain rates of 10<sup>−3</sup>/s and 2500/s.</p>
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<p>The fracture surfaces of compressed samples of TMC0 and TMC2: (<b>a</b>,<b>b</b>) the fracture surface of TMC0; (<b>c</b>,<b>d</b>) the fracture surface of TMC2. The inset showed detailed dimple morphologies at higher magnifications.</p>
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<p>Thre-dimensional topographies of samples with different mass fractions after shock compression at a strain rate of 2500/s: (<b>a</b>) TMC0, (<b>b</b>) TMC1, (<b>c</b>) TMC2, and (<b>d</b>) TMC3.</p>
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<p>SEM images of samples with different mass fractions after an impact load at a strain rate of 2500/s: (<b>a</b>) TMC0, (<b>b</b>) TMC1, (<b>c</b>) TMC2, and (<b>d</b>) TMC3. The inset shows detailed dimple morphologies at higher magnifications.</p>
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14 pages, 22258 KiB  
Article
The Influence of Laser Process Parameters on the Adhesion Strength between Electroless Copper and Carbon Fiber Composites Determined Using Response Surface Methodology
by Xizhao Wang, Jianguo Liu, Haixing Liu, Zhicheng Zhou, Zhongli Qin and Jiawen Cao
Micromachines 2023, 14(12), 2168; https://doi.org/10.3390/mi14122168 - 29 Nov 2023
Viewed by 839
Abstract
Laser process technology provides a feasible method for directly manufacturing surface-metallized carbon fiber composites (CFCs); however, the laser’s process parameters strongly influence on the adhesion strength between electroless copper and CFCs. Here, a nanosecond ultraviolet laser was used to fabricate electroless copper on [...] Read more.
Laser process technology provides a feasible method for directly manufacturing surface-metallized carbon fiber composites (CFCs); however, the laser’s process parameters strongly influence on the adhesion strength between electroless copper and CFCs. Here, a nanosecond ultraviolet laser was used to fabricate electroless copper on the surface of CFCs. In order to achieve good adhesion strength, four key process parameters, namely, the laser power, scanning line interval, scanning speed, and pulse frequency, were optimized experimentally using response surface methodology, and a central composite design was utilized to design the experiments. An analysis of variance was conducted to evaluate the adequacy and significance of the developed regression model. Also, the effect of the process parameters on the adhesion strength was determined. The numerical analysis indicated that the optimized laser power, scanning line interval, scanning speed, and pulse frequency were 5.5 W, 48.2 μm, 834.0 mm/s, and 69.5 kHz, respectively. A validation test confirmed that the predicted results were consistent with the actual values; thus, the developed mathematical model can adequately predict responses within the limits of the laser process parameters being used. Full article
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<p>Schematic diagram of the fabrication process of laser-induced copper plating on CFC surface.</p>
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<p>Nanosecond ultraviolet laser 3D process system: (<b>a</b>) equipment photograph and (<b>b</b>) schematic diagram.</p>
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<p>SEM images of pristine CFC surface (<b>a</b>) and laser-ablated CFC surface (<b>b</b>–<b>f</b>); (<b>c</b>,<b>e</b>) are the local magnifications of (<b>b</b>,<b>d)</b>, respectively. Laser power for (<b>b</b>,<b>d</b>,<b>f</b>) is 2.5 W, 5 W and 7 W, respectively, while other laser parameters (<span class="html-italic">U</span> = 40 μm, <span class="html-italic">V</span> = 300 mm/s, <span class="html-italic">f</span> = 60 kHz) remained unchanged and were scanned only once with the laser.</p>
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<p>Specimen photograph of electroless copper pattern on CFC surface.</p>
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<p>Schematic diagram of vertical pulling force measurement.</p>
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<p>Perturbation plot showing the effect of all factors on the adhesion strength.</p>
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<p>Interaction effect of laser power and scanning line interval on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Interaction effect of laser power and scanning speed on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Interaction effect of laser power and pulse frequency on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Interaction effect of scanning line interval and scanning speed on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Interaction effect of scanning speed and pulse frequency on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Interaction effect of scanning line interval and pulse frequency on adhesion strength: (<b>a</b>) contour plot and (<b>b</b>) 3D surface plot.</p>
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<p>Plots of the actual vs. predicted on adhesion strength.</p>
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15 pages, 7102 KiB  
Article
Effects of Building Directions on Microstructure, Impurity Elements and Mechanical Properties of NiTi Alloys Fabricated by Laser Powder Bed Fusion
by Shuo Wang, Xiao Yang, Jieming Chen, Hengpei Pan, Xiaolong Zhang, Congyi Zhang, Chunhui Li, Pan Liu, Xinyao Zhang, Lingqing Gao and Zhenzhong Wang
Micromachines 2023, 14(9), 1711; https://doi.org/10.3390/mi14091711 - 31 Aug 2023
Viewed by 978
Abstract
For NiTi alloys prepared by the Laser Powder Bed Fusion (LPBF), changes in the building directions will directly change the preferred orientation and thus directly affect the smart properties, such as superelasticity, as well as change the distribution state of defects and impurity [...] Read more.
For NiTi alloys prepared by the Laser Powder Bed Fusion (LPBF), changes in the building directions will directly change the preferred orientation and thus directly affect the smart properties, such as superelasticity, as well as change the distribution state of defects and impurity elements to affect the phase transformation behaviour, which in turn affects the smart properties at different temperatures. In this study, the relationship between impurity elements, the building directions, and functional properties; the effects of building directions on the crystallographic anisotropy; phase composition; superelastic properties; microhardness; geometrically necessary dislocation (GND) density; and impurity element content of NiTi SMAs fabricated by LPBF were systematically studied. Three building directions measured from the substrate, namely, 0°, 45° and 90°, were selected, and three sets of cylindrical samples were fabricated with the same process parameters. Along the building direction, a strong <100>//vertical direction (VD) texture was formed for all the samples. Because of the difference in transformation temperature, when tested at 15 °C, the sample with the 45° orientation possessed the highest strain recovery of 3.2%. When tested at the austenite phase transformation finish temperature (Af)+10 °C, the 90° sample had the highest strain recovery of 5.83% and a strain recovery rate of 83.3%. The sample with the 90° orientation presented the highest microhardness, which was attributed to its high dislocation density. Meanwhile, different building directions had an effect on the contents of O, C, and N impurity elements, which affected the transformation temperature by changing the Ni/Ti ratio. This study innovatively studied the impurity element content and GND densities of compressive samples with three building directions, providing theoretical guidance for LPBFed NiTi SMA structural parts. Full article
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<p>(<b>a</b>) Morphology of Ni<sub>50.8</sub>Ti<sub>49.2</sub> powder, (<b>b</b>) actual view of LPBFed NiTi SMA samples, (<b>c</b>) scanning strategy implemented in this research and (<b>d</b>) schematic of LPBFed NiTi SMA samples.</p>
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<p>Optical microstructure of (<b>a</b>) 0°, (<b>b</b>) 45° and (<b>c</b>) 90° samples (the rolling direction (RD) and transverse direction (TD) planes are the observation planes).</p>
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<p>The contents of carbon, oxygen and nitrogen in the virgin powder and 0°, 45° and 90° samples.</p>
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<p>Schematic of the EBSD collection position for the (<b>a</b>) 0°, (<b>b</b>) 45° and (<b>c</b>) 90° samples: (<b>a1</b>–<b>c1</b>) are IPF orientation maps of LPBFed NiTi SMAs along the normal direction; (<b>a2</b>–<b>c2</b>) are IPF orientation maps of LPBFed NiTi SMAs along the rolling direction; (<b>a3</b>–<b>c3</b>) are IPF orientation maps of LPBFed NiTi SMAs along the transverse direction; and (<b>a4</b>–<b>c4</b>) are corresponding {001}, {110} and {111} pole figures of the 0°, 45° and 90° samples.</p>
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<p>(<b>a</b>–<b>c</b>) EBSD analyses of the 0° sample. (<b>d</b>–<b>f</b>) EBSD analyses of the 45°sample. (<b>g</b>–<b>i</b>) EBSD analyses of the 90°sample. (<b>a</b>,<b>d</b>,<b>g</b>) Phase composition analyses. (<b>b</b>,<b>e</b>,<b>h</b>) KAM analyses. (<b>c</b>,<b>f</b>,<b>i</b>) Grain boundary distribution analyses.</p>
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<p>(<b>a</b>) GND distribution of the 0° sample, (<b>b</b>) 45° sample and (<b>c</b>) 90° sample and their corresponding (<b>d</b>) GND density values.</p>
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<p>(<b>a</b>) Bright field image and selected area electron diffraction in the corresponding circle region for the 0° sample (matrix and Ti<sub>2</sub>Ni phase). (<b>b</b>) Bright field image and selected electron diffraction in the corresponding elliptic region for the 0° sample.</p>
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<p>(<b>a</b>,<b>d</b>) TEM morphology of 0° samples. (<b>b</b>,<b>e</b>) TEM morphology of 45° samples. (<b>c</b>,<b>f</b>) TEM morphology of 90° samples.</p>
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<p>(<b>a</b>) DSC curves of 0°, 45° and 90° samples. (<b>b</b>) Corresponding Ni content of 0°, 45° and 90° samples.</p>
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<p>Microhardness of 0°, 45° and 90° samples.</p>
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<p>Compressive engineering stress-engineering strain curves for 0°, 45° and 90° samples (<b>a</b>) tested at ambient temperature (≈15 °C) and (<b>b</b>) tested at Af + 10 °C.</p>
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17 pages, 7014 KiB  
Article
Superelastic NiTi Functional Components by High-Precision Laser Powder Bed Fusion Process: The Critical Roles of Energy Density and Minimal Feature Size
by Shuo Qu, Liqiang Wang, Junhao Ding, Jin Fu, Shiming Gao, Qingping Ma, Hui Liu, Mingwang Fu, Yang Lu and Xu Song
Micromachines 2023, 14(7), 1436; https://doi.org/10.3390/mi14071436 - 18 Jul 2023
Cited by 2 | Viewed by 1472
Abstract
Additive manufacturing (AM) was recently developed for building intricate devices in many fields. Especially for laser powder bed fusion (LPBF), its high-precision manufacturing capability and adjustable process parameters are involved in tailoring the performance of functional components. NiTi is well-known as smart material [...] Read more.
Additive manufacturing (AM) was recently developed for building intricate devices in many fields. Especially for laser powder bed fusion (LPBF), its high-precision manufacturing capability and adjustable process parameters are involved in tailoring the performance of functional components. NiTi is well-known as smart material utilized widely in biomedical fields thanks to its unique superelastic and shape-memory performance. However, the properties of NiTi are extremely sensitive to material microstructure, which is mainly determined by process parameters in LPBF. In this work, we choose a unique NiTi intricate component: a robotic cannula tip, in which material superelasticity is a crucial requirement as the optimal object. First, the process window was confirmed by printing thin walls and bulk structures. Then, for optimizing parameters precisely, a Gyroid-type sheet triply periodic minimal-surface (G-TPMS) structure was proposed as the standard test sample. Finally, we verified that when the wall thickness of the G-TPMS structure is smaller than 130 μm, the optimal energy density changes from 167 J/m3 to 140 J/m3 owing to the lower cooling rate of thinner walls. To sum up, this work puts forward a novel process optimization methodology and provides the processing guidelines for intricate NiTi components by LPBF. Full article
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<p>Designing models and scanning path of (<b>a</b>) thin wall structure, (<b>b</b>) bulk structure, and (<b>c</b>,<b>d</b>) LED and VED distribution with process parameters.</p>
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<p>Models of NiTi components: (<b>a</b>) robotic cannula tip, (<b>b</b>) assembly of tip FE model, (<b>c</b>) G-TPMS lattice (unit cell), and (<b>d</b>) assembly of G-TPMS FE model.</p>
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<p>Characterization of NiTi original powder. (<b>a</b>,<b>b</b>) SEM observations at different magnifications, (<b>c</b>) XRD patterns, and (<b>d</b>) DSC curves.</p>
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<p>TWS characterizations: (<b>a</b>) Cross-sectional morphologies, (<b>b</b>) wall thicknesses of TWS samples, (<b>c</b>) XRD patterns, and (<b>d</b>) DSC analyses of phase transformation behaviors.</p>
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<p>Microstructural characterization of cubes fabricated with different parameters. (<b>a</b>) Depth of molten pools. (<b>b</b>) Half-width of molten pools. (<b>c</b>) Depth-to-width ratios of molten pools. (<b>d</b>–<b>i</b>) Side surface morphologies of cubes.</p>
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<p>Phase compositions and transformation behaviors of as-printed samples using different parameters: (<b>a</b>) XRD profiles, (<b>b</b>) DSC curves, (<b>c</b>) Mp and Ap values determined from (<b>b</b>) as functions of VED.</p>
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<p>Shape recovery behavior of NiTi samples of P5V6/P5V10/P7V6/P7V10 (<b>a</b>) same stress compression, (<b>c</b>) same strain compression and (<b>b</b>,<b>d</b>) irreversible/ recovered strain and recovery ratio of corresponding samples.</p>
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<p>FE results of stress distribution of (<b>a</b>–<b>c</b>) G-type TPMS lattice under 6% compressed strain (<b>a</b>) front view, (<b>b</b>) cross-section view, (<b>c</b>) local surface, (<b>d</b>–<b>f</b>) cannula tip with a bend, (<b>d</b>) front view, (<b>b</b>) side view, and (<b>c</b>) local surface.</p>
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<p>(<b>a</b>–<b>c</b>) Images of as-fabricated NiTi G-TPMS lattice structures with different relative densities of 10%/20%/40%, and (<b>d</b>–<b>f</b>) SEM images of corresponding TPMS lattices.</p>
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<p>Shape recovery properties of G-TPMS structures, loading-unloading responses of different RD (10%, 20%, 40%) (<b>a</b>–<b>c</b>) at stress control, (<b>g</b>–<b>i</b>) at strain control, irreversible/recovered strain and recovered ratio of TPMS with different RD (<b>d</b>–<b>f</b>) at stress control, and (<b>j</b>–<b>l</b>) at strain control.</p>
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<p>As-printed robotic cannula tip using P7V10 parameters: (<b>a</b>) Model, (<b>b</b>) top position by OM, (<b>c</b>) top cross-section by OM, (<b>d</b>) middle position by SEM, and (<b>e</b>) high-magnification SEM image of local position.</p>
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<p>Superelastic properties of NiTi robotic cannula tip using P7V10 and P5V6 parameters at room temperature.</p>
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17 pages, 9229 KiB  
Article
Influence of Aging Treatment Regimes on Microstructure and Mechanical Properties of Selective Laser Melted 17-4 PH Steel
by Dongdong Dong, Jiang Wang, Chaoyue Chen, Xuchang Tang, Yun Ye, Zhongming Ren, Shuo Yin, Zhenyu Yuan, Min Liu and Kesong Zhou
Micromachines 2023, 14(4), 871; https://doi.org/10.3390/mi14040871 - 18 Apr 2023
Cited by 3 | Viewed by 1647
Abstract
Aging is indispensable for balancing the strength and ductility of selective laser melted (SLM) precipitation hardening steels. This work investigated the influence of aging temperature and time on the microstructure and mechanical properties of SLM 17-4 PH steel. The 17-4 PH steel was [...] Read more.
Aging is indispensable for balancing the strength and ductility of selective laser melted (SLM) precipitation hardening steels. This work investigated the influence of aging temperature and time on the microstructure and mechanical properties of SLM 17-4 PH steel. The 17-4 PH steel was fabricated by SLM under a protective argon atmosphere (99.99 vol.%), then the microstructure and phase composition after different aging treatments were characterized via different advanced material characterization techniques, and the mechanical properties were systematically compared. Coarse martensite laths were observed in the aged samples compared with the as-built ones, regardless of the aging time and temperature. Increasing the aging temperature resulted in a larger grain size of the martensite lath and precipitation. The aging treatment induced the formation of the austenite phase with a face-centered cubic (FCC) structure. With prolonged aging treatment, the volume fraction of the austenite phase increased, which agreed with the EBSD phase mappings. The ultimate tensile strength (UTS) and yield strength gradually increased with increasing aging times at 482 °C. The UTS reached its peak value after aging for 3 h at 482 °C, which was similar to the trend of microhardness (i.e., UTS = 1353.4 MPa). However, the ductility of the SLM 17-4 PH steel decreased rapidly after aging treatment. This work reveals the influence of heat treatment on SLM 17-4 steel and proposes an optimal heat-treatment regime for the SLM high-performance steels. Full article
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<p>(<b>a</b>) Surface morphology of the 17-4PH steel powder; (<b>b</b>) scheme of the tensile test specimens used for the SLM fabrication.</p>
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<p>Microstructures of the SLM 17-4 PH steel under as-built conditions: (<b>a</b>) SEM; (<b>b</b>) IPF map; (<b>c</b>) phase distribution; (<b>d</b>) grain boundary map.</p>
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<p>Microstructural evolution of the aged SLM 17-4 PH steel at various aging temperatures for 1 h: (<b>a</b>) 382 °C; (<b>b</b>) 482 °C; (<b>c</b>) 582 °C; (<b>d</b>) 682 °C.</p>
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<p>Microstructure features of the aged SLM 17-4 steel at 482 °C for different holding times: (<b>a</b>) 0.5 h; (<b>b</b>) 2 h; (<b>c</b>) 3 h; (<b>d</b>) 5 h.</p>
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<p>EBSD characterizations of the SLM 17-4 PH steel samples under different conditions: (<b>a</b>–<b>c</b>) aged samples at 482 °C for 1 h; (<b>d</b>–<b>f</b>) aged at 482 °C for 3 h; (<b>g</b>–<b>i</b>) aged at 582 °C for 1 h. IPF images are shown in the first row, grain boundary distribution in the second row, and phase mapping in the third row.</p>
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<p>XRD spectra of the SLM-manufactured 17-4 PH steel samples under different (<b>a</b>) aging temperatures and (<b>b</b>) aging times.</p>
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<p>Typical microstructural evolution of the different aged states: (<b>a</b>) as-built; (<b>b</b>) under-aged; (<b>c</b>) adequate-aged; (<b>d</b>) over-aged.</p>
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<p>Microhardness variation of the SLM-manufactured 17-4 PH steel samples after aging treatments under different (<b>a</b>) temperatures and (<b>b</b>) holding times.</p>
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<p>Mechanical properties of the SLM 17-4 PH steel samples under different post-aging treatment conditions: (<b>a</b>,<b>b</b>) strain-stress curves and (<b>c</b>,<b>d</b>) key indicator statistics. First row: mechanical properties at different aging temperatures for 1 h. Second row: mechanical properties at different aging times at 482 °C.</p>
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<p>Fractographic features of the SLM 17-4 PH steel samples under different conditions: (<b>a</b>) as-built; (<b>b</b>) aged at 482 °C for 1 h; (<b>c</b>) aged at 482 °C for 3 h; (<b>d</b>) aged at 482 °C for 3 h.</p>
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15 pages, 12948 KiB  
Article
Laser Powder Bed Fusion of 316L Stainless Steel: Effect of Laser Polishing on the Surface Morphology and Corrosion Behavior
by Jun Liu, Haojun Ma, Lingjian Meng, Huan Yang, Can Yang, Shuangchen Ruan, Deqin Ouyang, Shuwen Mei, Leimin Deng, Jie Chen and Yu Cao
Micromachines 2023, 14(4), 850; https://doi.org/10.3390/mi14040850 - 14 Apr 2023
Cited by 3 | Viewed by 1958
Abstract
Recently, laser polishing, as an effective post-treatment technology for metal parts fabricated by laser powder bed fusion (LPBF), has received much attention. In this paper, LPBF-ed 316L stainless steel samples were polished by three different types of lasers. The effect of laser pulse [...] Read more.
Recently, laser polishing, as an effective post-treatment technology for metal parts fabricated by laser powder bed fusion (LPBF), has received much attention. In this paper, LPBF-ed 316L stainless steel samples were polished by three different types of lasers. The effect of laser pulse width on surface morphology and corrosion resistance was investigated. The experimental results show that, compared to the nanosecond (NS) and femtosecond (FS) lasers, the surface material’s sufficient remelting realized by the continuous wave (CW) laser results in a significant improvement in roughness. The surface hardness is increased and the corrosion resistance is the best. The microcracks on the NS laser-polished surface lead to a decrease in the microhardness and corrosion resistance. The FS laser does not significantly improve surface roughness. The ultrafast laser-induced micro-nanostructures increase the contact area of the electrochemical reaction, resulting in a decrease in corrosion resistance. Full article
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<p>(<b>a</b>) SEM image and (<b>b</b>) size distribution of 316L stainless steel powders.</p>
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<p>Actual images of the (<b>a</b>) CW, (<b>b</b>) FS, and (<b>c</b>) NS laser processing systems.</p>
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<p>(<b>a</b>) Surface roughness of the polished samples with different laser pulse widths. (<b>b</b>) Object picture of the LPBF-ed 316L stainless steel.</p>
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<p>Surface morphologies of the (<b>a</b>) original, (<b>b</b>) CW, (<b>c</b>) NS, and (<b>d</b>) FS laser-polished 316L stainless steel surfaces.</p>
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<p>Schematic illustrating the laser polishing with different pulse widths.</p>
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<p>XRD patterns of the LPBF-ed 316L stainless steel before and after laser polishing.</p>
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<p>Cross-sectional micrographs of the (<b>a</b>) original, (<b>b</b>) CW, (<b>c</b>) NS, and (<b>d</b>) FS laser-polished 316L stainless steel surfaces.</p>
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<p>(<b>a</b>) Microhardness distributions and (<b>b</b>) average hardness of original and laser-polished samples.</p>
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<p>Potentiodynamic polarization curves of original and laser-polished samples.</p>
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<p>Measured and simulated (<b>a</b>) Nyquist curves, (<b>b</b>) Bode impedance, and (<b>c</b>) Bode phase angle of original and laser-polished samples. (<b>d</b>) Electrochemical equivalent circuit model.</p>
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<p>Surface corrosion morphologies of the (<b>a</b>) original, (<b>b</b>) CW, (<b>c</b>) NS, and (<b>d</b>) FS laser-polished 316L stainless steel samples.</p>
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<p>Corrosion mechanism diagram of the (<b>a</b>) original and (<b>b</b>) laser-polished 316L stainless steel.</p>
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<p>Comparison of polarization curves of initial and laser-polished (<b>a</b>) P-SS and (<b>b</b>) SS.</p>
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<p>The influence of laser energy density and scanning speed on the roughness of (<b>a</b>) CW, (<b>b</b>) NS, and (<b>c</b>) FS laser-polished LPBF-ed stainless steel surfaces. (<b>d</b>) The influence of processing times on the roughness of laser-polished surfaces.</p>
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14 pages, 7307 KiB  
Article
Process Optimization and Tailored Mechanical Properties of a Nuclear Zr-4 Alloy Fabricated via Laser Powder Bed Fusion
by Changhui Song, Zhuang Zou, Zhongwei Yan, Feng Liu, Yongqiang Yang, Ming Yan and Changjun Han
Micromachines 2023, 14(3), 556; https://doi.org/10.3390/mi14030556 - 27 Feb 2023
Cited by 1 | Viewed by 1632
Abstract
A nuclear Zr-4 alloy with a near full density was fabricated via laser powder bed fusion (LPBF). The influences of process parameters on the printability, surface roughness, and mechanical properties of the LPBF-printed Zr-4 alloy were investigated. The results showed that the relative [...] Read more.
A nuclear Zr-4 alloy with a near full density was fabricated via laser powder bed fusion (LPBF). The influences of process parameters on the printability, surface roughness, and mechanical properties of the LPBF-printed Zr-4 alloy were investigated. The results showed that the relative density of the Zr-4 alloy samples was greater than 99.3% with the laser power range of 120–160 W and the scanning speed range of 600–1000 mm/s. Under a moderate laser power in the range of 120–140 W, the printed Zr-4 alloy possessed excellent surface molding quality with a surface roughness less than 10 µm. The microstructure of the printed Zr-4 alloy was an acicular α phase with an average grain size of about 1 µm. The Zr-4 alloy printed with a laser power of 130 W and a scanning speed of 400 mm/s exhibited the highest compression strength of 1980 MPa and the highest compression strain of 28%. The findings demonstrate the potential in the fabrication of complex Zr-4 alloy parts by LPBF for industrial applications. Full article
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<p>(<b>a</b>) Powder morphology of the Zr-4 alloy; (<b>b</b>) the schematic of the orthogonal scanning strategy; (<b>c</b>) geometries of the compressive sample model.</p>
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<p>Effects of process parameters on the relative density of the Zr-4 alloy: (<b>a</b>) variation of relative density against the laser power and scanning speed; (<b>b</b>) iso-density diagram; (<b>c</b>) variation of the relative density against the energy density.</p>
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<p>Macroscopic morphologies of the LPBF-printed Zr-4 samples with different process parameters.</p>
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<p>Effects of process parameters on the top surface roughness of the LPBF-printed Zr-4 alloy: (<b>a</b>) variation of the top surface roughness against the laser power and scanning speed; (<b>b</b>) iso-roughness diagram; (<b>c</b>) variation of the top surface roughness against the energy density.</p>
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<p>Top surface profiles under different laser powers (the scanning speed was fixed as 1100 mm/s): (<b>a</b>) <span class="html-italic">P</span> = 100 W; (<b>b</b>) <span class="html-italic">P</span> = 130 W; (<b>c</b>) <span class="html-italic">P</span> = 150 W; (<b>d</b>) <span class="html-italic">P</span> = 180 W.</p>
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<p>Metallographic images of the Zr-4 alloy printed using a laser power of 130 W and a scanning speed of 1000 mm/s along different planes: (<b>a</b>) the transverse plane; (<b>b</b>) the longitudinal plane.</p>
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<p>XRD pattern of the LPBF-printed Zr-4 alloy obtained using a laser power of 130 W and a scanning speed of 1000 mm/s.</p>
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<p>Compressive properties of the Zr-4 alloy at different laser powers and scanning speeds: (<b>a</b>) compressive curves at different scanning speeds; (<b>b</b>) variation of the compressive strength against the scanning speed (<span class="html-italic">P</span> = 130 W); (<b>c</b>) compressive curves at different laser powers; (<b>d</b>) variation of the compressive strength against the laser power (<span class="html-italic">V</span> = 1000 mm/s).</p>
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<p>Compression fractures of the Zr-4 alloy under different laser parameters: (<b>a</b>,<b>d</b>) <span class="html-italic">P</span> = 130 W and <span class="html-italic">V</span> = 400 mm/s; (<b>b</b>,<b>e</b>) <span class="html-italic">P</span> = 130 W and <span class="html-italic">V</span> = 1000 mm/s; (<b>c</b>,<b>f</b>) <span class="html-italic">P</span> = 130 W and <span class="html-italic">V</span> = 1400 mm/s; (<b>g</b>,<b>i</b>) <span class="html-italic">P</span> = 100 W and <span class="html-italic">V</span> = 1000 mm/s; (<b>h</b>,<b>j</b>) <span class="html-italic">P</span> = 200 W and <span class="html-italic">V</span> = 1000 mm/s.</p>
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15 pages, 4931 KiB  
Article
High Reflectivity and Thermal Conductivity Ag–Cu Multi-Material Structures Fabricated via Laser Powder Bed Fusion: Formation Mechanisms, Interfacial Characteristics, and Molten Pool Behavior
by Qiaoyu Chen, Yongbin Jing, Jie Yin, Zheng Li, Wei Xiong, Ping Gong, Lu Zhang, Simeng Li, Ruiqi Pan, Xiya Zhao and Liang Hao
Micromachines 2023, 14(2), 362; https://doi.org/10.3390/mi14020362 - 31 Jan 2023
Cited by 16 | Viewed by 2820
Abstract
Ag and Cu have different advantages and are widely used in key fields due to their typical highly electrical and thermal conductive (HETC) properties. Laser powder bed fusion (LPBF), an innovative technology for manufacturing metallic multi-material components with high accuracy, has expanded the [...] Read more.
Ag and Cu have different advantages and are widely used in key fields due to their typical highly electrical and thermal conductive (HETC) properties. Laser powder bed fusion (LPBF), an innovative technology for manufacturing metallic multi-material components with high accuracy, has expanded the application of Ag–Cu in emerging high-tech fields. In this study, the multi-material sandwich structures of Ag7.5Cu/Cu10Sn/Ag7.5Cu were printed using LPBF, and the formation mechanism, interface characteristics, and molten pool behavior of the Ag7.5Cu/Cu10Sn (A/C) and Cu10Sn/Ag7.5Cu (C/A) interfaces were studied to reveal the influence of different building strategies. At the A/C interface, pre-printed Ag7.5Cu promoted Marangoni turbulence at a relatively low energy density (EA/C = 125 J/mm3). Due to the recoil pressure, the molten pool at the A/C interface transformed from a stable keyhole mode to an unstable keyhole mode. These phenomena promoted the extensive migration of elements, forming a wider diffusion zone and reduced thermal cracking. At the C/A interface, the molten pool was rationed from the conduction mode with more pores to the transition mode with fewer defects due to the high energy density (EC/A = 187.5 J/mm3). This work offers a theoretical reference for the fabrication of HETC multi-material structures via LPBF under similar conditions. Full article
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<p>(<b>a</b>,<b>b</b>) SEM images of Ag7.5Cu and Cu10Sn powders, respectively; particle size distribution of (<b>c</b>) Ag7.5Cu powders and (<b>d</b>) Cu10Sn powders.</p>
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<p>Schematic illustration of LPBF process for fabricating Ag7.5Cu/Cu10Sn/Ag7.5Cu multi-material samples: (<b>a</b>) building strategy and parameters; (<b>b</b>) printing process.</p>
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<p>Optical images of two interfaces: (<b>a1</b>) macroscopic images of the A/C interface; (<b>a2</b>) enlarged view of area A in (<b>a1</b>); (<b>b1</b>) macroscopic images of C/A interface; (<b>b2</b>) enlarged view of area (B) in (<b>b1</b>). Orange arrows indicate the building direction (BD).</p>
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<p>Characteristics of two interfaces after etching: (<b>a</b>) mesoscopic morphology at A/C interface; (<b>b</b>) enlarged view of area A in (<b>a</b>); (<b>c</b>) mesoscopic morphology at C/A interface; (<b>d</b>) enlarged view of area B in (<b>c</b>). Orange arrows indicate the building direction (BD).</p>
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<p>Elemental distributions at A/C interface: (<b>a</b>) SEM image; (<b>b</b>) EDS mapping of (<b>a</b>); (<b>c</b>–<b>f</b>) showing elemental distributions of Cu, Ag, Sn, O, respectively; (<b>g</b>) EDS mapping of area A in (<b>a</b>); (<b>h</b>–<b>j</b>) showing elemental distributions of Cu, Ag, O, respectively. Orange arrow indicates the building direction (BD).</p>
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<p>Elemental distributions at C/A interface: (<b>a</b>) SEM image; (<b>b</b>) EDS mapping of (<b>a</b>); (<b>c</b>–<b>f</b>) showing elemental distributions of Ag, Cu, Sn, O, respectively. Orange arrow indicates the building direction (BD).</p>
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<p>EDS line scan results along the scan path 1 (<b>a</b>) and 2 (<b>b</b>) presented in <a href="#micromachines-14-00362-f005" class="html-fig">Figure 5</a>a and <a href="#micromachines-14-00362-f006" class="html-fig">Figure 6</a>a, respectively.</p>
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<p>Melting mode of A/C interface in multi-material LPBF: (<b>a</b>) schematic illustration of molten pool behavior; (<b>b</b>) molten pool morphology at A/C interface. Orange arrows indicate the building direction (BD).</p>
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<p>Melting mode of C/A interface in multi-material LPBF: (<b>a</b>) schematic illustration of molten pool behavior; (<b>b</b>) molten pool morphology at C/A interface. Orange arrows indicate the building direction (BD).</p>
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<p>Scheil–Gulliver solidification curves of Ag7.5Cu and Cu10Sn.</p>
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Review

Jump to: Editorial, Research

25 pages, 11049 KiB  
Review
Four-Dimensional Micro/Nanorobots via Laser Photochemical Synthesis towards the Molecular Scale
by Yufeng Tao, Liansheng Lin, Xudong Ren, Xuejiao Wang, Xia Cao, Heng Gu, Yunxia Ye, Yunpeng Ren and Zhiming Zhang
Micromachines 2023, 14(9), 1656; https://doi.org/10.3390/mi14091656 - 24 Aug 2023
Cited by 3 | Viewed by 1717
Abstract
Miniaturized four-dimensional (4D) micro/nanorobots denote a forerunning technique associated with interdisciplinary applications, such as in embeddable labs-on-chip, metamaterials, tissue engineering, cell manipulation, and tiny robotics. With emerging smart interactive materials, static micro/nanoscale architectures have upgraded to the fourth dimension, evincing time-dependent shape/property mutation. [...] Read more.
Miniaturized four-dimensional (4D) micro/nanorobots denote a forerunning technique associated with interdisciplinary applications, such as in embeddable labs-on-chip, metamaterials, tissue engineering, cell manipulation, and tiny robotics. With emerging smart interactive materials, static micro/nanoscale architectures have upgraded to the fourth dimension, evincing time-dependent shape/property mutation. Molecular-level 4D robotics promises complex sensing, self-adaption, transformation, and responsiveness to stimuli for highly valued functionalities. To precisely control 4D behaviors, current-laser-induced photochemical additive manufacturing, such as digital light projection, stereolithography, and two-photon polymerization, is pursuing high-freeform shape-reconfigurable capacities and high-resolution spatiotemporal programming strategies, which challenge multi-field sciences while offering new opportunities. Herein, this review summarizes the recent development of micro/nano 4D laser photochemical manufacturing, incorporating active materials and shape-programming strategies to provide an envisioning of these miniaturized 4D micro/nanorobots. A comparison with other chemical/physical fabricated micro/nanorobots further explains the advantages and potential usage of laser-synthesized micro/nanorobots. Full article
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<p>Schematic illustration of this review, covering three main sections: 1. laser-associated 4D manufacturing approaches and programming strategies around shape programming, which mostly operate on high-resolution two-photon polymerization and differ from macroscopic extrusion, material jetting, or other 3D printing methods; 2. stimuli-responsive materials, especially functional hydrogels/polymers, inorganic nonmetallic materials, and their nanocomposites; 3. future prospective interdisciplinary usage via 4D micro/nanofabrication is potentially applicable to micro/nanomechanics, adaptive optics, and bio-sciences. The organization logic throughout this manuscript follows this order: laser synthesis → smart materials → the programming strategies of 4D micro/nanorobotics → self-driven mechanism → application and comparison.</p>
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<p>(<b>a</b>) Single–photon absorption at relatively short-wavelength laser projection, green-light-triggered fluorescence absorption, typical two-photon absorption, multi-photon absorption at infrared wavelength laser projection. (<b>b</b>) There are four representative smart materials used in laser photochemistry for robotic applications: stimuli-responsive hydrogel, shape memory polymer, liquid metal elastomer, and protein materials.</p>
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<p>(<b>a<sub>1</sub></b>) Illustration of laser direct writing system and (<b>a<sub>2</sub></b>) its optical principle; (<b>b<sub>1</sub></b>–<b>b<sub>6</sub></b>) The current optical principle for high-freedom formation has developed to new categories: 2D spatial modulator (SLM) + 1D stage; the high-speed digital mirror (DMD) + 1D stage; the rotational substrate + projector; the newly-emerged 3D galvanometer with dynamically tunable focus lens; integrated 3D stage; 3D stage + beam splitting for paralleled fabrication.</p>
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<p>(<b>a</b>) The classical soft–rigid dual layer for shape bending. (<b>b</b>) The comprehensively enhanced shape reconfiguration of meta mechanical structure (biomimetic cilia). The simulation using finite element analysis matches well with experiment. (<b>c</b>) Optical micrographs of different shape transition states of woodpile photonic crystal microstructures regulated by the laser stimulation. There are eight positions of laser spot as indicated by the arrows. (<b>d</b>) Meta-structure-enhanced flower-shaped microclamp using a laser beam as photon stimuli. These figures are reproduced from Ref. [<a href="#B82-micromachines-14-01656" class="html-bibr">82</a>] with copyright permission. The scale bar is 10 µm. The scale bars of (<b>b</b>–<b>d</b>) are 10 µm.</p>
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<p>(<b>a<sub>0</sub></b>) Illustration of laser focus voxel during the laser synthesis process. The red ellipse denotes the focused laser point inside the precursor material. The other figure is the section view of the laser-scanned interlaced nanowire/interspacing nanostructure reproduced from Ref. [<a href="#B18-micromachines-14-01656" class="html-bibr">18</a>], which is known as a heterojunction nanostructure in Ref. [<a href="#B12-micromachines-14-01656" class="html-bibr">12</a>]. (<b>a<sub>1</sub></b>) The nanowire-based heterojunction scanning strategies in monolayer. (<b>a<sub>2</sub></b>,<b>a<sub>3</sub></b>) The accumulated intermolecular force realized “bracelet” and chiral torsion, respectively. (<b>b<sub>1</sub></b>–<b>b<sub>3</sub></b>) The out-of-plane bent biomimetic hand, flower, and grippers. These figures are reproduced from Ref. [<a href="#B12-micromachines-14-01656" class="html-bibr">12</a>] with copyright permission from the authors. The scale bars of (<b>a<sub>2</sub></b>,<b>a<sub>3</sub></b>) are 50 µm, and the scale bars of (<b>b<sub>1</sub></b>–<b>b<sub>3</sub></b>) are all 50 µm.</p>
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<p>(<b>a<sub>1</sub></b>) Fabrication procedures for the magnetically driven rotary microfilter reproduced from Ref. [<a href="#B86-micromachines-14-01656" class="html-bibr">86</a>] with permission from © The Optical Society. (<b>a<sub>2</sub></b>,<b>a<sub>3</sub></b>) SEM images of the two-photon polymerization fabricated filter on a flat surface and embedded inside a fluidic channel. The scale bars are 20 μm. (<b>b</b>) Example of temperature response: a woodpile and spiral disk thermally change their dimension and lead to coloration change. Reproduced from Ref. [<a href="#B90-micromachines-14-01656" class="html-bibr">90</a>]. The scale bars represent 20 μm.</p>
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<p>(<b>a</b>) Illustration of dual-layer structure shape changing by pH variation. Reproduced from Ref. [<a href="#B96-micromachines-14-01656" class="html-bibr">96</a>]. (<b>b</b>) The reverse gripping action from a pair of designed protein cantilevers, where the scale bar is 5 μm. (<b>c</b>) The swelling/shrinkage of a cube shape made of proteins by two-photon polymerization. Reproduced from Ref. [<a href="#B96-micromachines-14-01656" class="html-bibr">96</a>]. The scale bar is 10 μm. (<b>d</b>–<b>f</b>) The authors of Ref. [<a href="#B83-micromachines-14-01656" class="html-bibr">83</a>] demonstrate a composite-material micro claw robot responsive to pH variation, where SU–8 photoresist works as the rigid part and BSA is bovine serum protein, which is polymerized on the claw to form the flexible muscle.</p>
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<p>The authors of Ref. [<a href="#B104-micromachines-14-01656" class="html-bibr">104</a>] present demonstrations of innovative technologies that enable the creation of complex 3D reconfigurable micro-architectures. These architectures are made possible through the use of advanced micromachines, such as microstents, microcages, and micro-umbrellas (<b>a</b>–<b>c</b>). These micromachines are capable of achieving various forms of reconfiguration, including rapid and precise uniaxial contraction, biaxial contraction, and articulated-lever folding. This level of flexibility allows for a wide range of applications in fields such as robotics and biomedical engineering. The process used to create these structures is known as 4DLW (four-dimensional direct laser writing). It involves several steps, including the embedding of deformation-amplifying mechanisms, the design of the 4DLW system, FEA prediction to optimize performance, the actual 4D direct writing process using lasers or other techniques, and finally, shape-morphing to achieve the desired configuration. The pictures are reproduced from Ref. [<a href="#B104-micromachines-14-01656" class="html-bibr">104</a>].</p>
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<p>The focusing and imaging performances of a batch of protein-based compound eyes reproduced from Ref. [<a href="#B118-micromachines-14-01656" class="html-bibr">118</a>] with the author’s permission. The compound eye under investigation is composed of ommatidia, each measuring 10 μm in diameter and 3 μm in height. (<b>a</b>) Displays a 3D laser confocal microscopy image capturing the detailed structure of the compound eye. To assess its imaging capabilities, the researchers analyzed the performance from the inner part to the outer part of the compound eye, as depicted in (<b>b</b>–<b>d</b>). (<b>e</b>) The schematic of the optical setup used to measure the imaging performance of compound eyes.</p>
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<p>The researchers of Ref. [<a href="#B123-micromachines-14-01656" class="html-bibr">123</a>] achieved one-step 4D printing of shape-morphing microrobots for HeLa cell treatment. The fabricated magnetic microrobots (in the shapes of crabs and fishes) can undergo shape-morphing to achieve targeted drug release for treating cancer cells. (<b>a</b>) Schematic of the magnetic shape-morphing microfish (SMMF) for targeted doxorubicin (DOX) release to treat cancer cells by shape-morphing. (<b>b</b>) Main compositions and schematic of pH-responsive hydrogels, where AAc is acrylic acid, DPEPA is the cross-linker thdipentaerythritol penta acrylate, and EMK is the photoinitiator 4,4′–bis–(diethylamino)benzophenone. (<b>c</b>) Four-dimensional printing with a designable point density to encode shape-morphing. (<b>d</b>) Scanning electron microscopy (SEM) images of the gel pores in the tail and body (inset images). (<b>e</b>) Optical images of the 4D fish and crab, illustrating the opening and closure of the fins and claws, respectively. (<b>f</b>,<b>g</b>) Schematic procedures and time-lapse images of I. selecting, II. tightly gripping, III. transporting, and IV. releasing targeted cargo by the 4D crab. Scale bars: (<b>d</b>) 1 μm, and inset images, 5 μm; (<b>e</b>) 25 μm; (<b>f</b>,<b>g</b>) 50 μm. All pictures here are reproduced from Ref. [<a href="#B123-micromachines-14-01656" class="html-bibr">123</a>].</p>
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<p>The researchers of Ref. [<a href="#B82-micromachines-14-01656" class="html-bibr">82</a>] have successfully printed and demonstrated a functioning microscale artificial heart. Their schematic of the heart structure is depicted in (<b>a</b>). To assess its functionality, the opening amplitude of the aortic valve is examined under different light stimulation powers, as shown in (<b>b</b>), and optical micrographs captured the changes in valve opening as a result of varying light stimulation. Furthermore, optical micrographs were taken to compare the appearance of the microheart with and without light stimulation, as seen in (<b>c</b>). It is worth noting that this remarkable piece of technology has incredibly small dimensions, measuring merely 80 × 120 × 60 µm<sup>3</sup>, as indicated by the schematic illustration inset, in which the scale bar denotes 20 µm.</p>
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<p>The other existing 4DM/NR types reported, including their features, prospective applications, and research interests.</p>
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<p>Comparative analysis of four different currently studied 4DM/NRs in terms of applications, fabrication, unique advantages, design capability, and feature size, where laser photochemically synthesized 4D robots possess the most comprehensive advantage, slowing the application range covering micro/nano optics, electronics, and robotics with flexible geometric design outperforming the human-cultured microorganisms or nanoparticle-shaped Janus robotics. Moreover, the laser synthesis allows multi-function integration in tiny volumes requires only one-step fabrication, which is much more efficient and beneficial to shorten the design circles.</p>
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