Single-Composition Functionally Graded Ti-6Al-4V for Mimicking Composite Material Fiber Reinforcement Through Post-Heating Laser Scanning

Single-Composition Functionally Graded Ti-6Al-4V for Mimicking Composite Material Fiber Reinforcement Through Post-Heating Laser Scanning | Research Square window.SnipcartSettings = { analytics: { enabled: false } }; (function() { var accessVector = localStorage.getItem('access_vector') || ''; window.dataLayer = window.dataLayer || []; if (accessVector) { window.dataLayer.push({ user: { profile: { profileInfo: { snid: accessVector } } } }); } })(); (function(w,d,s,l,i){w[l]=w[l]||[];w[l].push({'gtm.start':new Date().getTime(),event:'gtm.js'});var f=d.getElementsByTagName(s)[0],j=d.createElement(s),dl=l!='dataLayer'?'&l='+l:'';j.async=true;j.src='https://www.googletagmanager.com/gtm.js?id='+i+dl;f.parentNode.insertBefore(j,f);})(window,document,'script','dataLayer','GTM-K279D39R'); Browse Preprints In Review Journals COVID-19 Preprints AJE Video Bytes Research Tools Research Promotion AJE Professional Editing AJE Rubriq About Preprint Platform In Review Editorial Policies Our Team Advisory Board Help Center Sign In Submit a Preprint Cite Share Download PDF Research Article Single-Composition Functionally Graded Ti-6Al-4V for Mimicking Composite Material Fiber Reinforcement Through Post-Heating Laser Scanning Ahmet Alptug TANRIKULU, Aditya Ganesh-Ram, Hamidreza Hekmatjou, and 3 more This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-4751892/v1 This work is licensed under a CC BY 4.0 License Status: Published Journal Publication published 19 Dec, 2024 Read the published version in The International Journal of Advanced Manufacturing Technology → Version 1 posted 5 You are reading this latest preprint version Abstract Process-induced microstructure modification was investigated for the strengthening mechanism of Laser Powder Bed Fusion Fabricated (LPBF) Ti-6Al-4V material. An innovative approach by mimicking the fiber structure of the composite materials was studied. Different cylindrical reinforcement diameters were selected in the LPBF-fabricated Ti-6Al-4V samples to replicate the function of the carbon fibers in composite materials, providing stiffness and reinforcement in the matrix. The corresponding regions of the assigned Reinforcement shape at each layer were exposed to a secondary laser scan through the sample during the fabrication. Multi-scan laser scanning strategies, involving a combination of laser power and scan speed were employed after the melting laser scan to maximize the relative density of the material. The optimized post-heating laser scan enhanced the relative density (> 99.95%), recrystallized the α and α′ phases’ lath morphology, modified the lattice structure, transformed the initial microstrain mode, and enhanced the inherent grain texture of the PBF fabricated Ti-6Al-4V. The tailored microstructure achieved a 46.5% higher yield strength (YS) accompanied by a 99.3% higher elongation. Functionally graded microstructure LPBF Ti-6Al-4V in situ microstructure modification post-heating laser scan multiple laser scan Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 Figure 10 Figure 11 Figure 12 1. Introduction LPBF stands as one of the most common Additive Manufacturing (AM) techniques for metallic parts and has been captivating wide attention due to its fine feature resolution and superiorities in complex geometry fabrication. This led to the realization of bio-inspired [ 1 ] and lightweight component [ 2 ] fabrication in the near-net shape without the necessity of machining. Additionally, LPBF helps to transform sub-assemblies into a single part, which decreases production costs and time [ 3 ]. Exceptional mechanical properties of the Ti-6Al-4V such as remarkable specific strength, excellent corrosion resistivity, biocompatibility, and superb fracture toughness explain its widespread use in aerospace [ 4 – 6 ] and biomedical industries [ 7 – 9 ]. In addition, its adaptability to various manufacturing processes such as AM broadens its applications across various engineering industries. LPBF fabrication capabilities and exceptional material properties of Ti-6Al-4V advanced the popularity of AM applications mostly in the aerospace industry [ 10 – 12 ]. As a result of the increasing attention, the compelling combination of the LPBF process and the Ti-6Al-4V material has recently earned approval from the Federal Aviation Administration (FAA) for a flight critic component fabrication [ 13 ]. However, there is a certified application, microstructure complexity, and the anisotropic mechanical behavior of LPBF-fabricated Ti-6Al-4V are still not standardized. There are many studies in which the process and the material were comprehensively investigated, yet the challenges have not been fully addressed by researchers. In the LPBF technique, a high-power laser beam is precisely focused onto micron-sized areas. The focused laser beam interacts with the loose powder bed at extremely high scanning speeds, resulting in rapid solidification and cooling rates [ 14 , 15 ]. Thus, the LPBF technique leads to higher residual stresses in the part due to accelerated shrinkage and contraction arising from the processing method [ 16 ]. Additionally, the heat dissipation through the built material underneath the molten metal leads to directional cooling, resulting in a grain texture in the microstructure [ 17 – 19 ]. This induces anisotropy in the mechanical properties of the fabricated part which is directionally dependent. This directionally dependent mechanical response of the final part is considered an extensive problem that needs to be addressed [ 20 , 21 ]. Some widely used approaches include changes in design and setting up the fabrication orientation which adds up to the production time and cost including the number of test qualifications required [ 22 ]. Materials researchers have been studying this highly stressed and oriented microstructure to envision the impact of the fabrication process and explore novel methodologies for modifying its mechanical response. Post-heat treatment (HT) has been widely studied as a possible technique to modify the microstructure for desired improvements in mechanical response [ 23 – 25 ]. The impact of the various HTs on the LPBF-fabricated microstructure and its mechanical response has been studied comprehensively [ 26 – 28 ]. Reports indicated an elongation improvement of up to 15.8% [ 24 ] with a striking reduction in the strength of LPBF-fabricated Ti-6Al-4V [ 29 ]. Additionally, materials researchers have applied different strengthening mechanisms to modify the complex microstructure and address the challenges related to the mechanical properties of the LPBF-fabricated Ti-6Al-4V material [ 30 – 33 ]. One of the notable achievements reported was a 26.50% in the material’s strength with the addition of TiC particles to the melt pool of Ti-6Al-4V which resulted in a drastic reduction of the elongation [ 34 ]. It is coherent that there is an inverse relation between strengthening and plastic deformability. It was reported that the investigated complementary processes to modify the microstructure either enhanced the plastic deformation ability or the mechanical strength of the LPBF-fabricated Ti-6Al-4V. Here, a process-induced microstructure modification for the material’s reinforcement has been proposed and studied which enhanced the mechanical strength and plastic deformation ability for LPBF-fabricated Ti-6Al-4V. Although strength and plastic deformation are inversely proportional, results proved that with the studied innovative reinforcement approach it is possible to achieve remarkable improvement in strength along with a significant enhancement in elongation for LPBF-fabricated Ti-6Al-4V. Previous studies presented that it is possible to modify the LPBF-fabricated Ti-6Al-4V microstructure locally [ 35 – 37 ] and fully [ 38 ] regarding the applied scanning strategy during the fabrication. In the present study, a post-heating laser scan was introduced upon the melting scan for the corresponding regions of the selected areas for each layer where the fiber texture of the composite materials was mimicked for reinforcement. The post-heating laser scan was studied at different laser power values and scan speeds to monitor the effect on microstructure. It was observed that optimized post-heating laser scan parameters have a significant effect on the inherent process-induced defects. The post-heating laser scan parameters that delivered the lowest porosity were assigned to the selected regions to modify the LPBF-fabricated Ti-6Al-4V material’s microstructure. The novel approach, which was inspired by the composite material’s nature, performed a tremendous strengthening in LPBF-fabricated Ti-6Al-4V material. Contrary to the common approaches in the literature, according to the results of the presented study, it is evident that the proposed in-situ strengthening enhances the strength along with the elongation of the material without the necessity of any complementary thermal processing or any additional compound during the fabrication. 2. Materials and Methods 2.1 Materials Ti-6Al-4V Grade 5 powder used for the fabrication was gas atomized and supplied by EOS North America (Pflugerville, TX, USA). The particle diameter of the powder ranged from 20 µm to 80 µm with a chemical composition of (wt.%) 5.50–6.75 Al, 3.50–4.50 V, 0.20 O, 0.05 N, 0.08 C, 0.015 H, 0.30 Fe, and the balance was Ti [ 39 ]. Microstructure samples fabricated with the dimensions of 20 mm × 6 mm × 6 mm and test coupons for tensile testing fabricated in dog-bone geometry with the dimensions and the applied regions exposed to the post-heating laser scan depicted in Fig. 1 . The widely accepted tensile testing standard ASTM E8/E8M ‘Standard Test Methods for Tension Testing of Metallic Materials’ does not have rectangular cross-section test specimen dimensions smaller than 25 mm gauge length. Thus, the authors designed a representative specimen geometry close to the standard dimension, which is suitable for multiple specimen fabrication in a single batch for the LPBF printer employed during the experimental study. 2.2 Methods Samples were fabricated using Laser Powder Bed Fusion (LPBF) technology with an EOS M290 printer (EOS GmbH, Electro Optical Systems, Krailling, Germany) using Ytterbium fiber laser power of 400 W. To quantize the effect of the applied post-heating scan after melting the laser track, post-heating energy density was calculated from the energy density equation reported by Thijs et al. (Eq. 1 ) [ 40 ]. $$\:{E}_{v}=\frac{P}{v.h.t}$$ 1 Central composite design (CCD) [ 41 ] was used for the post-heating laser scan process parameters in a variety of laser scan speeds between 650mm/s to 1950mm/s and laser power between 140W to 252W. In this design of experiment (DoE) 15 different variants were defined by the Box-Behnken method. Figure 2 illustrates the scanning sequences of the reference (Fig. 2 (a)), layerwise post-heated (Fig. 2 (b)), and layerwise locally post-heated applications (Fig. 2 (c)). The suggested process parameters by the material supplier are 280 W laser power, 1300 mm/s scan speed, 120 µm hatch spacing, 100 µm laser spot size with a Gaussian distribution of energy, and 40 µm of layer thickness with 67° angle stripes scanning strategy [ 42 ]. These parameters were used for the melting laser scan on each layer initially and defined as the default parameters. Specimens were exposed first to the melting laser scan with default parameters and this was followed by a post-heating laser scan for the assigned regions of the tensile coupons. This scanning sequence was applied with variable post-heating energy densities (14.96 J/mm 3 to 80.77 J/mm 3 ) to assess the microstructure response to the post-heating and investigate the mechanical properties of the final geometry. Scanning strategy, scanning pattern, layer thickness, hatch spacing, and hatch angle were kept at the value of suggested process parameters. The building plate temperature was preheated to 80 °C and maintained during the fabrication to reduce the thermal gradient of the first layer and delamination of the first layers. All specimens were cut from the building plate using a wire Electrical Discharge Machining (EDM) cutter (EDM Network, Inc., Sugar Grove, IL, USA). Scanning Electron Microscopy (SEM) imaging studies were performed for porosity, α-phase lath width, and grain morphology caused by various post-heating energy inputs. Samples were cut out by a TECHCUT 5™ precision low-speed cutter (Allied High-Tech Products, Inc., Rancho Dominguez, CA, USA) from the center of the specimen along the building plane, prior to the sample preparation. Samples were cold mounted and prepared by grinding from 320 to 1200 grit size of SiC sandpaper. Afterward, the first step of polishing was performed on a DiaMat ® polishing cloth with 1 µm diamond suspension. Polishing finalized with 0.04 µm colloidal silica suspension on Red Final C ® polishing pad used to obtain scratch-free, mirror-like finish sample surfaces. Polished samples were rinsed in micro-organic soap and cleaned with isopropyl alcohol. Samples were etched with Kroll’s reagent (1–3 mL HF, 2–6 mL HNO 3 , 100 mL water) to identify the grain boundaries and phases of the microstructure. Image J [ 43 ], an image analysis software, was used to calculate the porosity level of each microstructure. The porosity distribution was determined from at least three different regions at 2 magnification levels (500x and 1000x). Image J was also used for the lath width calculation of the α-phase. For image processing, microstructure images were first converted to RGB stack-type grayscale images prior to setting the auto contrast level. Thresholding was generated to create a clear contrast between α/α′ phases’ lath borders. Particles were analyzed between 0.2 µm to 2.0 µm then total counts of the particle at each size were calculated for the mean value. This calculation made at least 6 different images for statistically meaningful data from every sample’s building plane orientation. X-ray diffraction analyses were performed for phase identification, calculation of the lattice parameters, and orientations of the microstructure of each sample. A Bruker D8 Advance X-ray diffractometer (Bruker Corporation, Madison, WI, USA) was used for the analysis with 1.5406 Å Cu k-alpha wavelength, 40 mA current, 40 kV voltage at room temperature, and the measurements were taken with step intervals of 0.5° and a scan speed of 1sec/step while the 2θ varied between 20° to 80°. Lattice parameters were calculated according to Bragg’s law (Eq. ( 2 )) where d, is inter-planar spacing, a and c are the lattice parameters and h, k, l are the Miller indices. $$\:\frac{1}{{d}^{2}}=\:\frac{4}{3}\:\left(\frac{{h}^{2}+hk+\:{k}^{2}}{{a}^{2}}\:\right)+\:\frac{{l}^{2}}{{c}^{2}}$$ 2 $$\:\lambda\:=2d\:sinϴ$$ The Williamson – Hall (W–H) model [ 44 ] was employed to assess the microstrain condition of the microstructure of the reference and post-heating laser scan application. The XRD data was utilized in the following equations (Eq. (3) (4) (5)). Peak broadening of the XRD data is caused by crystal imperfections and distortion which is related by ε ≈ βs / tanθ. The W–H plot was used for the calculation of the microstrain value. Si standard reflection (0.0013 rad) [ 45 ] was subtracted before strain analysis using W–H method. The Scherrer’s equation (Eq. (3)) derived to Eq. (5) where β is peak broadening, λ is the wavelength (Å). K is the Cu Ks (0.94), D is the crystallite size (nm) and θ is the peak position. D = \(\:\frac{\lambda\:\:K}{\beta\:\:cos\theta\:}\) (3) β = \(\:\sqrt{{{\beta\:}_{T}}^{2}-\:{{\beta\:}_{i}}^{2}}\) (4) β cosθ = \(\:\frac{\lambda\:\:K}{D}\) + 4ε sinθ (5) Shimadzu EHF E-Series (100kN) equipped with a 4830-servo controller (Shimadzu Scientific Instruments, Inc., Missouri City, TX, USA) was used for tensile testing. Strain measurements of the gauge region were made by using a digital image correlation (DIC) system. The surface strain and displacements were captured by tracking the patterns of the high-contrast speckles on the coupon surface. This contactless technique can measure the local strains at the fracture as well as the global strain during the loading of the coupons. Two 2.3MP CCD cameras, Grasshopper GS3-U3-23S6M (FLIR Systems, Inc., Santa Barbra, CA, USA) with a pixel array of 1920 x 1200 were used for image capturing. Processing of the captured images and correlation with the stress loading were made using VIC-3D® software (Correlated Solutions, Inc., Irmo, SC, USA). Considering the previous studies [ 46 , 47 ], the loading rate was set to 1.2 mm/min for all tests. 3. Results 3.1 Microstructure 3.1.1 Defect / Porosity Analysis The porosity levels corresponding to the selected post-heating laser power values and post-heating laser scan speeds were studied using the Box-Behnken DoE model. A total of fifteen post-heating laser power and scan speed variations were characterized and their effect on porosity was evaluated. SEM micrographs at various regions and magnification levels for each scenario revealed that the post-heating laser scan significantly impacted the inherent porosity level of L-PBF Ti-6Al-4V. The RSM plot for the post-heating laser power between 140–252W and post-heating laser scan speed between 650–1950 mm/s was depicted in Fig. 3 (a). It was confirmed that 650 mm/s post-heating laser scan speed delivered the minimum porosity levels for each post-heating laser scan power. Additionally, it was observed the post-heating laser power of 140W minimized the porosity during the experimental study. The relation between the post-heating laser scan speed and the porosity level of the microstructure at the constant post-heating laser scan power (140 W) was depicted in Fig. 3 (b). The porosity level of the reference sample without a complemental post-heating laser scan was measured at 0.47% ± 0.015 [ 47 ]. It was undoubted that a subsequent laser scan decreased the initial porosity level, and it was measured to be up to 90%. The denser microstructure of the post-laser scan can be ascribed to remelting [ 48 , 49 ]. The inherent porosity level of the L-PBF Ti-6Al-4V was minimized with the post-heating laser scan parameters of 140W laser power and 650mm/s laser scan speed. These optimized parameters delivered almost a fully dense (> 99.95%) microstructure and were subjected to further microstructural and mechanical testing as the post-heating laser scan sample and selected for the post-heating laser applications of the presented study. The microstructure response after the post-heating laser scan for circular reinforcement regions of diameters ∅0.4 mm, ∅0.6 mm, and ∅0.8 mm was illustrated in Fig. 3 (c), and the porosity levels were measured as 0.08 ± 0.01%, 0.07 ± 0.06%, 0.07 ± 0.07%, respectively. 3.1.2 Grain Morphology and Lattice Structure The microstructure of the Ti-6Al-4V, an α + β alloy, fabricated via LPBF consists of a greater number of α/α′ phases at room temperature, which exhibits a basketweave-like structure [ 50 ]. The lath width of the basketweave-like structure determines the mechanical response of the alloy [ 51 ]. The grain morphology of the Ti-6Al-4V alloy was assessed, and the response of the α/α′ phases’ lath structure to the applied processes was evaluated. Table 1 depicts the average lath width and the lath angle for each application. The average lath width of the samples was measured with image processing[ 43 ] of the SEM micrographs at magnification levels of 500x, 800x, 1200x, and 1500x. The lath width of the reference sample was measured to be 0.797 ± 0.005 µm. The highest lath width was observed in the microstructure samples which were fully exposed to the optimized post-heating laser scan (0.894 ± 0.051 µm). The lowest lath width was observed in the double-scanned regions of the ∅0.4 mm reinforcement application (0.687 ± 0.007). It was evident that an additional post-heating laser scan across the entire cross-section of the samples had a significant effect on lath width. Results showed a 12% increase in the lath width between the reference (no additional laser scan) and the sample fully exposed to the post-heating laser scan. The variation in lath width between the single and double-scanned regions in the microstructure of reinforcement applications was also evaluated. The limited application of the post-heating laser scan only to the projection of the reinforcement geometries on the samples’ cross-section did not have a major effect compared to the fully applied post-heating laser to the samples’ cross-section. The highest variation was observed in the ∅0.8 mm reinforcement application and calculated as a 3.6% increase with the addition of a post-heating laser scan. Table 1 HCP – Ti (α/α′ phases) lath width and angle. Reference (No additional laser scan) Fully Post-heated ∅0.4mm Reinforcement Scan ∅0.6mm Reinforcement Scan ∅0.8mm Reinforcement Scan Melting Scan (single scan region) Melting + Post-heating Scan (double scan region) Melting Scan (single laser region) Melting + Post-heating Scan (double laser region) Melting Scan (single laser region) Melting + Post-heating Scan (double laser scan) Ave. Lath Width (µm) 0.797 ± 0.005 0.894 ± 0.051 0.691 ± 0.006 0.687 ± 0.007 0.749 ± 0.007 0.727 ± 0.006 0.690 ± 0.010 0.715 ± 0.005 Ave. Lath Angle (°) 118.08 ± 2.69 81.88 ± 7.27 95.13 ± 3.77 98.38 ± 3.07 95.20 ± 1.99 98.00 ± 1.85 98.19 ± 0.81 94.36 ± 1.32 Lath structure micrograph images of the α/α′ phases of each application are shown in Fig. 4 . The representative images of the microstructure variation between the single-scan and double-scanned regions (projection of the reinforcement geometries on the cross-section) for ∅0.4, ∅0.6, and ∅0.8 mm reinforcement application is illustrated in Fig. 4 (c), (d), and (e) respectively. The lath width slightly decreased in the double-scanned scan regions for ∅0.4 mm and ∅0.6 mm reinforcement size. In opposition, the lath width was measured thicker in ∅0.8 mm reinforcement size at the double scanned regions. In addition to size, the angle of the α-colonies affects the deformation mechanism and the strength of the Ti-6Al-4V alloy [ 52 ]. The lath angle of the α/α′ phases was analyzed with image processing [ 43 ]. The lath angles with respect to their width have been presented in Fig. 5 . Lath sizes between the range of 0 to 2 µm have been plotted with their corresponding angles. It was observed that almost all the laths concentrated themselves either within 0º and 75º or between 75º and 180º. The lath densities in the measured window is found to be higher in the double exposed region than in the single exposed region as seen from Fig. 5 . This phenomenon was observed with all other reinforcement sizes tested. The investigated grain morphology of the α/α′ phases have a hexagonal close-packed (HCP) lattice structure. Lattice parameters HCP structure of the α/α′ phases were calculated according to Bragg’s law [ 53 ] and plotted in Fig. 6 . A reduction in both lattice parameters of a and c was observed (Fig. 6 (a) and (b)). Additionally, a strain on the lattice was observed with the applied post-heating laser scan. Figure 6 (c) shows the strain with a higher c/a ratio with the additional laser scan. The post-heating laser scan increased the c/a ratio of the lattice which is a result of the lower cooling rate [ 54 ] of the post-heating laser scan application. The W-H model was employed for further microstructure analysis to gain a better understanding of the strain and stress condition of the samples. Eq. (5) was considered as a y = mx + c equation and the equation was plotted as the W-H model in which the slope of this equation is the microstrain value [ 44 ]. According to the model, the initial microstrain condition of the microstructure at the reference sample without a complementary post-heating laser scan was determined as tension. The positive slope of the plotted model of the reference sample is shown in red in Fig. 6 (d). A remarkable change in the initial condition of the L-PBF Ti-6Al-4V was observed after the application of the post-heating laser scan. The plotted model of the post-heating laser scan shows a negative slope which indicates that the microstrain condition of the microstructure was turned out in compression mode. The effect of the tension and compression mode of the microstructure on the mechanical response will be discussed in the discussion section. 3.2 Compositional Analysis XRD Figure 7 depicts the XRD profiles of the reference and post-heated specimens. The highest intensity of Bragg’s peak was observed at the (101) plane on the XY plane of the reference sample. Despite the post-heating samples have similar peak patterns, it is noteworthy that the strongest peak intensity was observed at the (002) plane on the XY plane. The remarkable change in the peak intensities indicated that the majority of the grain orientation was modified with the applied post-heating laser scan along the (002) plane. 3.3 Mechanical Testing The mechanical response of the modified microstructure was quantified through tensile testing. The stress-strain plot is depicted in Fig. 8. The post-heating laser scan reinforcement strategy had a significant effect on the mechanical response of the material. It was observed that both ultimate tensile strength (UTS) and yield strength (YS) values were enhanced. A remarkable increase in the slope during elastic deformation led to a higher YS for each post-heating laser scan strategy applied in the present study. The enhancements in YS were 22.6%, 11.4%, 46.5%, and 34.6% for the reinforcement applications of fully post-heating, ∅0.4 mm, ∅0.6 mm, and ∅0.8 mm reinforcement size, respectively. The ∅0.6 mm reinforcement delivered an extensive advancement in UTS with a strength value of 1608 ± 122 MPa. This is followed by ∅0.8 mm reinforcement, fully post-heated application, and ∅0.4 mm reinforcement with the strength values of 1485 ± 91 MPa, 1335 ± 96 MPa, 1217 ± 44 MPa, respectively. Reinforcement geometries of ∅0.4 mm and ∅0.6 mm delivered exceptional elongations, which were 69.0% and 99.3% higher compared to the reference sample, respectively. On the contrary ∅0.8 mm reinforcement coupons and the fully post-heating coupons ended up with a slightly lower elongation compared to the reference sample. It was observed that the applied post-heating laser strategy changed the deformation during the tensile testing. Figure 9 depicts the DIC results of localized plastic deformation before fracture for each application. Results show that applied post-heating laser scan regardless the geometry of the scanning area, modified the deformation behavior of the LPBF-fabricated Ti-6Al-4V. Local deformation accumulated in various angles and locations after the application of the post-heating laser scan. 4. Discussions In the present study, an in-situ strengthening strategy during the LPBF process for Ti-6Al-4V was evaluated. A post-heating laser scan was employed upon the melting scan to maximize the relative density and modify the Ti-6Al-4V material’s microstructure in terms of α/α′ phases (HCP-Ti) grain and lattice structure. Furthermore, the complementary post-heating laser scans aimed to enhance the inherent grain texture of the LPBF-fabricated Ti-6Al-4V through directional solidification and cooling. The post-heating laser scan was applied both fully across the microstructure and only to the designated regions in the specimens’ cross-section. The fiber structure of the composite materials was replicated in the presented study, and reinforcement geometries with different diameters were assigned into the samples as the reinforcements during the design process and a building file was generated for the scan strategy for each application accordingly. The projection of these geometries onto the cross-section of the coupons was exposed to an additional post-heating laser scan which parameters minimized the inherent porosity value. The preliminary data of the microstructure, which was fully exposed to the post-heating laser scan, clearly indicated a strengthening effect. It is rational to observe a reduction in the material’s elongation for the strengthened materials [ 55 ]. With this strategy, ∼50% of the cross-section was aimed at strengthening, thus the reduction in the elongation would be limited compared to the fully post-heated sample. Results proved that the reinforcement strategy presented in this study improved the elongation significantly whereas the LPBF fabricated Ti-6Al-4V delivered higher strength compared to previous thermal processing studies. 4.1 Localized Post-heating Laser Scan Effect on Process-induced Defects The impact of the post-heating laser scan parameters (laser power (W), laser scan speed (mm/s)) on the process-induced porosity can be seen in Fig. 3 . (a). The figure provides significant insights regarding the correlation between post-heating laser scan parameters, such as laser power and scanning speed, and their impact on reducing the porosity level. It was observed the post-heating laser scan power of 140W and scanning speed of 650 mm/s delivered the lowest porosity level. Post-heating laser scan with 140W laser power and 650 mm/s scanning speed decreased the porosity level from 0.470–0.046%. Additionally, results indicated that the lowest porosity value for different post-heating laser powers (252W and 196W) was delivered with a scanning speed of 650 mm/s (Fig. 2 (b)). A similar effect was reported in re-melting studies with higher energy inputs to the powder bed[ 56 – 58 ] and Hot Isostatic Pressure (HIP) applications in which additional processing was required [ 59 , 60 ]. 4.2 α/α′ Phase Lath Structure Tailoring by Localized Post-heating Laser Scan The predominant stable phases in the LPBF-fabricated Ti-6Al-4V microstructure at room temperature were observed as α and α′ phases. Due to the complexity of the LPBF fabricated Ti-6Al-4V alloy’s microstructure it requires additional microstructure characterization tools to distinguish these phases from each other which is not the scope of the presented study. It has been a common practice in the literature to evaluate the microstructure of LPBF-fabricated Ti-6Al-4V alloy for its mechanical properties together as the α/α′ phases, α-Ti or HCP-Ti [ 61 ]. The difference between these phases depends on the cooling rate and their structure is distinct from each other due to the lath width. The higher cooling rate delivers a thinner lath width which is called as martensite and annotated as α′ phase, and the relatively slower cooling regions are α phases with a pattern called Widmanstätten [ 62 ]. It is rational to examine both phases together since the average lath width was considered for the microstructure investigation. In addition, both phases have an HCP lattice structure, which cannot be distinguished when computing the lattice parameters using XRD data. The impact of the post-heating laser scan on α-Ti lath width is listed in Table 1 . The application of the post-heating laser scan fully across the microstructure increased the average lath width of the material. A comparable effect was observed with the conventional HTs, however, the observed lath coarsening after the applied post-heating laser scan (12.17% increase) was below the reported HT applications; Zou et al. [ 63 ] applied heat treatment to L-PBF Ti-6Al-4V below the β-transus temperature (925°C/2hr/FC(7°C/min)) and authors reported a 40% increase on lath width, Lu et al. [ 64 ] applied a heat treatment above the β-transus temperature (1015°C/1hr/AC) and a 75% increase on lath width was reported. In addition to these conventional post-heat treatments, Karami et al. [ 65 ] reported a ∼110% increase with the application of hot isostatic processing (HIP) HIP (920°C/2hr/100MPa). Table 2 Effect of the post-HT on the mechanical behavior of the L-PBF Ti-6Al-4V Heat Treatment YS As-Built (MPa) YS HTed (MPa) As-Built Elongation (%) HTed Elongation (%) Change of YS (%) Change of Elongation (%) Etesami et al. [ 66 ] 900°/2hr/AC ∼1180 ∼1100 8.7 4.9 -6.77 -43.67 Simonelli et al. [ 67 ] 730°C/2h/FC 1075 ± 25(H) 967 ± 10(V) 974 ± 7(H) 937 ± 7(V) 7.6 ± 0.5(H) 8.9 ± 0.4(V) 7.0 ± 0.5(H) 9.6 ± 0.9(V) -9.39 -3.10 -8.57 7.86 Vilaro et al. [ 68 ] Supersolvus 1137 ± 20(H) 962 ± 47(V) 913 ± 7(H) 836 ± 64(V) 7.6 ± 2(H) 1.7 ± 0.3(V) 8.9 ± 1(H) 7.9 ± 1(V) -19.70 -13.09 17.11 364.7 Subtransus 1137 ± 20(H) 962 ± 47(V) 944 ± 8(H) 925 ± 14(V) 7.6 ± 2(H) 1.7 ± 0.3(V) 8.5 ± 1(H) 7.5 ± 2(V) -19.70 -3.84 11.84 341.1 Low Temperature 1137 ± 20(H) 962 ± 47(V) 965 ± 16(H) 900 ± 101(V) 7.6 ± 2(H) 1.7 ± 0.3(V) 9.5 ± 1(H) 1.9 ± 0.8(V) -15.12 -6.44 25.00 11.76 Vrancken et al. [ 69 ] 540°C/5hr/WQ 1110 ± 9 1118 ± 39 7.28 ± 1.12 5.36 ± 2.02 0.72 -26.37 1020°C /2hr/FC 1110 ± 9 760 ± 19 7.28 ± 1.12 14.06 ± 2.53 -31.53 93.13 850°C/5hr/FC 1110 ± 9 909 ± 6 7.28 ± 1.12 Premature failure -18.10 N/A 1050°C/0.5hr/AC + 730°C/2hr/AC 1110 ± 9 822 ± 19 7.28 ± 1.12 12.74 ± 0.56 -25.94 75.00 Cao et al. [ 70 ] 800°C/2hr ∼1020(H) ∼950(V) ∼950(H) ∼850(V) ∼4 ∼4 ∼9 ∼6 -6.86 -10.52 125.00 50.00 Sabban et al. [ 71 ] 975°C − 875°C (Cyclic HT) /24hr/AC 1047 ± 23(H) 1043 ± 18(V) 865 ± 19(H) 849 ± 12(V) 10 ± 1(H) 12 ± 1(V) 18 ± 1(H) 16 ± 1(V) -17.38 -18.60 80.00 33.33 Zhang et al. [ 72 ] 900°C/6hr/AC 1112 ± 8 864 ± 3 7 ± 1 10 ± 1 -22.30 42.86 750°C/2hr/FC 1351 1185 3.14 3.4 -12.29 8.28 Yan et al. [ 73 ] 800°C/2hr/FC + AC 1065 996 6 7 -6.47 16.67 1080°C/2hr/FC + AC 1065 840 6 4 -21.12 -33.33 Kasperovich et al. [ 74 ] 900°C/2hr + 700°C/1hr /FC(10K/min) Annealed 600°C 986 990 ± 5 908 870 ± 15 11.9 8.1 ± 0.3 9.5 11.0 ± 0.5 -7.91 -12.12 -20.17 35.80 Facchini et al .[ 75 ] Fully Post Heating Laser Scan ∅0.4 mm Reinforcement Post Heating Laser Scan ∅0.6 mm Reinforcement Post Heating Laser Scan ∅0.8 mm Reinforcement Post Heating Laser Scan - - - - 1001 ± 38 1001 ± 38 1001 ± 38 1001 ± 38 1228 ± 80 1115 ± 44 1467 ± 85 1347 ± 62 3.26 ± 0.4 3.26 ± 0.4 3.26 ± 0.4 3.26 ± 0.4 4.28 ± 0.4 5.51 ± 0.2 6.50 ± 0.7 4.11 ± 0.2 22.6 11.4 46.5 34.6 31.3 69.0 99.3 26.1 α/α′ lath colonies decompose from the β-grain boundaries during the phase transformation below the allotropic transformation temperature. The cooling rate during the phase transformation defines the nucleation and grain growth of the precipitate phase. Faster cooling rates resulted in thinner laths with more randomly distributed structures since α/α′ nucleation starts irregularly inner side of the β-grain as well as the β-grain boundaries [ 50 ]. A schematic view of the α/α′ lath colonies formation is depicted in Fig. 10 . A slight decrease in the lath thickness of the α/α′ colonies was observed in the double-scanned regions of the ∅0.4 mm and ∅0.6 mm reinforcement applications. Authors considered this as a result of different cooling compared to the single scanned regions where microstructure inhomogeneity is higher due to the rapid and directional cooling [ 76 , 77 ]. The effective thermal conductivity of the Ti-6Al-4V powder bed during the melting scan is 0.13 W/mK [ 78 ] which is much less compared to the bulk Ti-6Al-4V. Findings revealed a linear relation between the temperature of the Ti-6Al-4V and its thermal conductivity, according to the study presented by Saini et al. [ 79 ] thermal conductivity of Ti-6Al-4V exceeds 20 W/mK at 1200°C. This value is almost 154 times higher than the thermal conductivity of the loose powder. The complementary post-heating process applied the high-temperature solidified Ti-6Al-4V material which has relatively higher thermal conductivity and led to a faster cooling rate and delivered thinner α/α′ colonies (Table 1 ). The reinforcement application of the ∅0.8 mm had a different response which will be evaluated in future studies. The angle at which the laths align themselves gives us an idea of the homogeneity in microstructure formation and thus the strength of the resulting part [ 80 ]. In-homogeneity in the grain orientations is one of the primary sources of dislocation sites from where the crack initiates before leading to failure upon mechanical loading. Figure 5 . helps us comment on the grain orientations observed in the reinforcement regions compared to non-reinforcement regions. Looking at the lath density concentrations, grain orientation homogeneity seems to improve within the reinforcement regions. This highlights that the resulting solid part comprises homogeneous and in-homogeneous grain orientations. It should also be noted that as the reinforcement size reduced, the largely variant lath densities in the reinforcement region when compared to the non-reinforcement regions seem to be reduced. This might be because of the fact that the volume of material receiving the higher energy density has a direct correlation to its effect on the lath formation in the neighboring regions. Bigger reinforcements transfer higher thermal energy to the non-processed regions thus making the entire region of a cross-section with uniformly orienting laths. The lath width of the α/α′ phase had a significant effect on the mechanical response of the L-PBF Ti-6Al-4V material [ 66 , 81 ]. Hadadzadeh et al. [ 81 ] attributed the high strength of L-PBF Ti-6Al-4V to finer α/α′ laths through the Hall-Petch effect[ 82 ] and Etesami et al [ 66 ] reported the remarkable effect of the α/α′ laths width on elongation during the tensile test. In the present study, lath coarsening was observed, and it is one of the reasons for the preferred elongation. 4.3 Localized Post-heating Laser Scan Effect on Crystallography The findings, as depicted in Fig. 6 , demonstrated the post-heating laser scan has a remarkable effect on the LPBF-fabricated Ti-6Al-4V lattice structure as well as the microstrain. An increase in the lattice parameters was reported in previous studies[ 83 , 84 ] with the application of the post-heat treatment. The increase in the lattice parameters was attributed to the higher diffusivity of the vanadium atoms[ 84 , 85 ] of Ti-6Al-4V during the post-heat treatment temperatures. Vanadium atoms diffused out of the HCP lattice and larger titanium atoms[ 86 ] occupied their positions which transformed the structure into a larger lattice. On the contrary to the conventional post-heat treatment applications, a slight decrease in the lattice parameters both a and c was observed with the application of the post-heating laser scan (Fig. 6 (a) & (b)). Lattice shrinkage can be explained by the vanadium atoms diffusion mechanism. It is well-known that additional heat leads to an increase in temperature which improves the solubility of the substitutional atoms in this case of the post-heating laser scan application it is vanadium atoms [ 87 ]. The increasing amount of the substitutional vanadium atoms leads to a decrease in the lattice parameters since vanadium has smaller atomic radii compared to titanium atoms that were substituted by vanadium during the post-heating laser scan. Compared to the conventional HTs, the post-heating laser scan exhibits a relatively higher cooling rate. The smaller lattice parameters of the post-heating laser scan can be rationalized with faster cooling rates with lower diffusivity, which limits the diffusion of the excessive vanadium atoms from their positions inside the HCP lattice. The previous study demonstrated that introducing additional laser scan to the powder bed exceeds the operation temperature, causing an increase in the affinity of titanium to oxygen [ 47 ]. This makes the molten metal more sensitive to oxidation, even under shield gas protection. The lattice strain measured in the presented study (Fig. 6 ) can be justified by the same phenomenon. Figure 11 depicts the representative image of the super-saturated HCP lattice with the octahedral position occupied by the oxygen atoms which strains the lattice along the c-axis. Addition to the lattice strain Fig. 6 depicts the decrease in both a and c lattice parameters, result of the trapped vanadium atoms in the HCP lattice which occupies the titanium atom positions with smaller atomic radii. It is known that the lattice distortion due to the interstitial oxygen atoms strengthens the LPBF-fabricated Ti-6Al-4V material [ 47 , 88 ]. 4.4 Mechanical Response of the Material to the Reinforcement by Localized Post-heating The resulting tensile strength and elongation on the reinforcement applications have been studied (Fig. 8.) It was observed that post-heating through a second laser scan resulted in a remarkable enhancement in the material’s strength. It is rational to have a lower elongation with the increase in strength after the strengthening process [ 34 ]. This is noticeable when the post-heating laser scan was applied fully across the cross-section of the material (Fig. 8. (a) gray line). Considering that, when the post-heating laser was carried out in limited localized regions (circular area of the reinforcement geometry projection on the sample cross-section), there seems to be a significant increase in the elongation along with tensile strength for the 0.4 mm and 0.6 mm reinforcement diameter (Fig. 8. (a) green and yellow line). It is interesting to note that the highest elongation was observed for the 0.6 mm reinforcement size reinforcements which also had the highest tensile strength among all the test cases. This fascinating occurrence of obtaining higher strength and higher elongation can be explained by the reinforcement matrix formation due to the combination of finer and coarser α/α′ lath regions obtained within the cross-section of a solidified Ti6Al4 microstructure. It further helped to direct research attention toward identifying the limits at which the matrix strengthening occurs depending on the reinforced area of the post-heated section. It should also be noted that the shape of the region that is being post-heated might influence the properties as well which need to be further investigated. The common practice of strengthening in the literature has been studied by introducing additional elements and components to the microstructure of the LPBF-fabricated Ti-6Al-4V such as nitrogen, and titanium-carbide. Liu et al. [ 89 ] investigated the in-situ nitrogen strengthening of the LPBF-fabricated Ti-6Al-4V by introducing nitrogen to the build chamber through the shield gas. The highest improvement in the YS was reported as 20.01% with a drastic reduction in elongation. However, the authors reported a significant improvement in the material’s strength, the elongation of the strengthened material was decreased by almost half of the initial condition. He et al. [ 90 ] studied the strengthening of the Ti-6Al-4V with the addition of LaB 6 to the LPBF process. In their study, the highest improvement in the material’s strength was 14.50% with a 37.2% reduction in elongation. TiC addition to the Ti-6Al-4V components during the LPBF process is also a preferred way to reinforce the material [ 34 , 91 ]. Jiang et al. [ 91 ] investigated the effect of TiC in Ti-6Al-4V during the LPBF process and the authors reported titanium matrix composites with TiC addition had a 10.68% higher strength with a very limited elongation. Tang et al. [ 34 ] in their TiC reinforcement study, it was reported that the highest improvement in strength was ∼26.50% with an elongation of 3.65% which is less than half of the initial as-built condition of the material. Previous studies have revealed that the strengthening of LPBF fabricated Ti-6Al-4V was limited to ∼26.50% and caused a notable reduction in elongation. The proposed innovative reinforcement strategy of post-heating laser scan was assigned to designated regions on the specimen. It was observed that the studied reinforcement strategy of post-heating laser scan resulted in a remarkable improvement of ∼50% in YS which is the highest enhancement in the strength among the previously reported studies. More importantly, a remarkable improvement in the elongation (∼100% improvement) was also achieved with the proposed composite additive manufacturing application for the first time. Thus, the elongation reduction due to the strengthening is promised to be controlled as well as improved for the engineering applications. Post-heating HT is one of the most popular complementary processes that was applied to modify the microstructure of the LPBF-fabricated Ti-6Al-4V. Table 2 depicts the mechanical response of the modified microstructure after the HT. However, there are some studies that reported a decrease both in strength and elongation, the general response after HT was a decrease in the strength and an increase in elongation. It is due to the lath coarsening and the stress relieving effect of the HT which is discussed previously. The studied post-heating laser scan strategy modified the LPBF Ti-6Al-4V microstructure by reforming the α/α′ phases lath structure (Table 1 . and Fig. 5 .), HCP lattice structure (Fig. 5 .), initial microstrain mode (Fig. 6 .) and the grain texture (Fig. 7 .). Figure 12 depicts the yield strength and the elongation of the LPBF fabricated Ti-6Al-4V material after conventional HT and the post-heating laser scan reinforcement application (green region). Considering the studies listed in Table 2 and Fig. 8. the proposed reinforcement application that mimicked the composite materials with a complementary post-heating laser scan of the limited regions of the cross-section during the fabrication promised to dismiss the thermal post-processing of LPBF fabricated Ti-6Al-4V with superior mechanical properties. A notable enhancement in YS was observed for each reinforcement application, attributed to the modification of the α/α′ colonies by localized post-heating laser scan and eliminated process-induced defects (Fig. 8). Compared to the reference sample each post-heating application had higher yielding point. It is known that the grain boundary network with respect to the population and connectivity enhances the polycrystalline materials [ 92 ]. At further deformation, modified grain boundary crystallography impacts the dislocation motion[ 93 ] which was observed in the present study with higher UTS values during the tensile testing (Fig. 7 ). 5. Conclusion The present study proposed an innovative strengthening strategy for the LPBF process by mimicking the fiber texture of the composite materials. The reinforcement shape was selected to replicate the fiber function of reinforcement in the matrix. Different reinforcement diameters were selected according to the resolution of the LPBF technology to study the effect of reinforcement size on the mechanical response of the material. The corresponding regions of the assigned reinforcement shape at each layer were exposed to a secondary laser scan through the sample during the fabrication. Studied microstructure clearly demonstrated that the optimized post-heating laser scan modified the LPBF-fabricated Ti-6Al-4V alloy’s microstructure by recrystallizing the α/α′ phases lath structure, stretching the HCP lattice, transforming the initial strain mode, and the inherent grain texture. Notably, the mechanical response of the tailored microstructure for reinforcement indicated a remarkable improvement in strength. The post-heating laser scan reinforcement application was observed to increase elongation, as well as the strength of the material for each reinforcement diameter. The results apparently indicated that the proposed innovative thermal processing of the LPBF-fabricated Ti-6Al-4V during the fabrication can alternate the requirement of the complementary post-processing of heat treatment to modify the microstructure for the desired mechanical response. Additionally, results promised to strengthen the material without the requirement of auxiliary components such as nitrides, or carbides which makes the LPBF process more challenging in non-uniform chemical composition distribution. Declarations Funding: this research received no external funding Conflict of interest : The authors declare no conflicts of interest Authors’ Contribution: Ahmet Alptug Tanrikulu : Conceptualization, writing-original-draft, characterization, methodology. Aditya Krishna Ganesh-Ram : writing-review-editing, testing, investigation, fabrication. Hamidreza Hekmatjou : investigation, data analysis, pre-processing. 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Rapid Prototyp J 16:450–459. https://doi.org/10.1108/13552541011083371 Present SJ, Taminger KM, Domack CS, Hemker KJ (2023) The Inhomogeneous Microstructure and Mechanical Properties of Ti–6Al–4V Additively Manufactured by Electron Beam Freeform Fabrication. Metall Mater Trans A 54:312–319. https://doi.org/10.1007/s11661-022-06874-0 Wang Q, Liu Z, Yang D, Mohsan AUH (2017) Metallurgical-based prediction of stress-temperature induced rapid heating and cooling phase transformations for high speed machining Ti-6Al-4V alloy. Mater Des 119:208–218. https://doi.org/10.1016/j.matdes.2017.01.076 Bartsch K, Bossen B, Chaudhary W et al (2022) Thermal Conductivity of Ti-6Al-4V in Laser Powder Bed Fusion. Front Mech Eng 8. https://doi.org/10.3389/fmech.2022.830104 Saini A, Pabla B, Dhami S (2016) Developments in cutting tool technology in improving machinability of Ti6Al4V alloy: A review. 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Addit Manuf 45:102003. https://doi.org/10.1016/j.addma.2021.102003 Ghio E, Cerri E (2022) Additive Manufacturing of AlSi10Mg and Ti6Al4V Lightweight Alloys via Laser Powder Bed Fusion: A Review of Heat Treatments Effects. Materials 15:2047. https://doi.org/10.3390/ma15062047 Kaschel FR, Vijayaraghavan RK, Shmeliov A et al (2020) Mechanism of stress relaxation and phase transformation in additively manufactured Ti-6Al-4V via in situ high temperature XRD and TEM analyses. Acta Mater 188:720–732. https://doi.org/10.1016/j.actamat.2020.02.056 Slater JC (1964) Atomic Radii in Crystals. J Chem Phys 41:3199–3204. https://doi.org/10.1063/1.1725697 Grewal G, Ikem S (1990) Particle coarsening behavior of α-β titanium alloys. Metall Trans A 21:1645–1654. https://doi.org/10.1007/BF02672579 Zou Z, Simonelli M, Katrib J et al (2021) Microstructure and tensile properties of additive manufactured Ti-6Al-4V with refined prior-β grain structure obtained by rapid heat treatment. Mater Sci Engineering: A 814:141271. https://doi.org/10.1016/j.msea.2021.141271 Liu L, Chen C, Zhao R et al (2021) In-situ nitrogen strengthening of selective laser melted Ti6Al4V with superior mechanical performance. Addit Manuf 46:102142. https://doi.org/10.1016/j.addma.2021.102142 He D, Wang H, Huang W et al (2023) Microstructure and Mechanical Properties of LaB6/Ti-6Al-4V Composites Fabricated by Selective Laser Melting. Met (Basel) 13:264. https://doi.org/10.3390/met13020264 Jiang Q, Li S, Guo S et al (2023) Comparative study on process-structure-property relationships of TiC/Ti6Al4V and Ti6Al4V by selective laser melting. Int J Mech Sci 241:107963. https://doi.org/10.1016/j.ijmecsci.2022.107963 Farabi E, Tari V, Hodgson PD et al (2020) On the grain boundary network characteristics in a martensitic Ti–6Al–4V alloy. J Mater Sci 55:15299–15321. https://doi.org/10.1007/s10853-020-05075-7 Lütjering G (1998) Influence of processing on microstructure and mechanical properties of (α + β) titanium alloys. Mater Sci Engineering: A 243:32–45. https://doi.org/10.1016/S0921-5093(97)00778-8 Cite Share Download PDF Status: Published Journal Publication published 19 Dec, 2024 Read the published version in The International Journal of Advanced Manufacturing Technology → Version 1 posted Editorial decision: Minor Revisions Needed 22 Nov, 2024 Reviewers agreed at journal 27 Jul, 2024 Reviewers invited by journal 20 Jul, 2024 Editor assigned by journal 18 Jul, 2024 First submitted to journal 17 Jul, 2024 You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. 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Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-4751892","acceptedTermsAndConditions":true,"allowDirectSubmit":false,"archivedVersions":[],"articleType":"Research Article","associatedPublications":[],"authors":[{"id":329525933,"identity":"a7beb8dd-8637-4517-bd1b-0a2a101ff878","order_by":0,"name":"Ahmet Alptug TANRIKULU","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAA6klEQVRIie3RsQrCMBCA4RShXQquJ4X2FVIKpYPiq7QU4qI4CKJboBBHV1/CwaVzIVCXoGtGRXBy6AMoGDcdjB0d8sMt4T44CEIm03/mNLDo++8v+Ifo2CgRJHrfbkGWjGe0NelupvVJCjLarkTUWOweIKcoQUdAcCfcLPqTUoxjsBgOqVvPtQTtC+SBIJOyIgQpYlFQVicC3kHeg/FRfLzm6jA8pMFNT/C+sKHHeBrLvHodllFw9SQUPMLqsLCUlxrSQ5Qzl8wSHfFldj6prwziY1Y0zdwfrB2+kzryWarGbr9uMplMpm89AcZbShJSn8zUAAAAAElFTkSuQmCC","orcid":"https://orcid.org/0000-0002-4693-4576","institution":"The University of Texas at Arlington","correspondingAuthor":true,"prefix":"","firstName":"Ahmet","middleName":"Alptug","lastName":"TANRIKULU","suffix":""},{"id":329525934,"identity":"dde68d10-356b-445a-b5c7-fb28303b8fc7","order_by":1,"name":"Aditya Ganesh-Ram","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Aditya","middleName":"","lastName":"Ganesh-Ram","suffix":""},{"id":329525935,"identity":"3bca4d97-ab13-4a5d-bd02-92921c56f4b1","order_by":2,"name":"Hamidreza Hekmatjou","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Hamidreza","middleName":"","lastName":"Hekmatjou","suffix":""},{"id":329525936,"identity":"3a4f802d-e3d9-4080-96c5-00b879781e1e","order_by":3,"name":"Sadman Hafiz Durlov","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Sadman","middleName":"Hafiz","lastName":"Durlov","suffix":""},{"id":329525937,"identity":"dcb4d4cc-dec4-4736-8847-bddeb947d22a","order_by":4,"name":"Md Najmus Salehin","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Md","middleName":"Najmus","lastName":"Salehin","suffix":""},{"id":329525938,"identity":"5d6d47d2-c967-43c8-9a2c-f0e7af364496","order_by":5,"name":"Amirhesam Amerinatanzi","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Amirhesam","middleName":"","lastName":"Amerinatanzi","suffix":""}],"badges":[],"createdAt":"2024-07-16 18:45:59","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-4751892/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-4751892/v1","draftVersion":[],"editorialEvents":[{"content":"https://doi.org/10.1007/s00170-024-14902-z","type":"published","date":"2024-12-19T15:57:36+00:00"}],"editorialNote":"","failedWorkflow":false,"files":[{"id":62732384,"identity":"6b97f26f-006b-4594-883f-da5091e76fbc","added_by":"auto","created_at":"2024-08-18 23:44:52","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":18177,"visible":true,"origin":"","legend":"\u003cp\u003eTensile test coupon dimensions.\u003c/p\u003e","description":"","filename":"1.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/e508142558ed6d78dfca7fb0.png"},{"id":62731172,"identity":"c45a0dcc-304c-4375-b641-be98f4166398","added_by":"auto","created_at":"2024-08-18 23:28:52","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":182413,"visible":true,"origin":"","legend":"\u003cp\u003eLaser scan sequence for (a) reference sample: single exposure with default process parameters, (b) Fully post-heated sample: double laser scan across the sample cross-section; first laser scan: melting with default process parameters, second laser scan: post-heating with various laser parameters, (c) Layerwise locally post-heated sample: first laser scan: melting across the sample cross-section, second laser scan: post-heating with various laser process parameters, only on the selected regions based on the reinforcement geometry (Regions marked in black) in the gauge cross-section represent the areas that were exposed to double scanning (Melting Laser Scan + Post-heating Laser Scan), the total area of the double scanned regions for the reinforcement geometries of (d) ∅0.4mm reinforcement diameters, (e)∅0.6mm reinforcement diameter, and (f) ∅0.8mm reinforcement diameter are 47.5%, 66.7%, and 55.4% respectively.\u003c/p\u003e","description":"","filename":"2.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/f02b55b7df699d19c03c647c.png"},{"id":62731174,"identity":"68c71062-c81b-4165-a488-c55c2bc7bf98","added_by":"auto","created_at":"2024-08-18 23:28:52","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":169044,"visible":true,"origin":"","legend":"\u003cp\u003ePorosity level was optimized at a post-heating laser scan speed of 650 mm/s for a variety of post-heating laser scan speeds. Post-heating laser power of 140W minimized the porosity of the microstructure. (a) RSM analysis of porosity in LPBF fabricated Ti-6Al-4V microstructure with varying post-heating laser scan power and speed. (b) Porosity values for various post-heating laser power at the constant post-heating laser scan speed (650mm/s), and various post-heating laser scan speeds at the constant laser power (140W). (c) Impact of different post-heating scanning areas on microstructural response to porosity.\u003c/p\u003e","description":"","filename":"3.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/d3cd182012a861e31e4ff869.png"},{"id":62731175,"identity":"565a6b02-04ae-4734-9ae8-1490c172f85f","added_by":"auto","created_at":"2024-08-18 23:28:53","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":819266,"visible":true,"origin":"","legend":"\u003cp\u003eSEM micrograph of LPBF fabricated Ti-6Al-4V; (a) microstructure of reference sample with no additional laser scan, (b) Thicker α/α′ lath structure (12% higher) after the application of the optimized post-heating laser scan fully across the cross-section, Lath structure variation between the double-scanned (melting laser scan + post-heating laser scan) regions (reinforcement processing geometry projection on the cross-section represented by dotted circle) and the single-scanned (only melting laser scan) regions for (c) ∅0.4 mm reinforcement size, (d) ∅0.6 mm reinforcement size, and (e) ∅0.8 mm reinforcement size.\u003c/p\u003e","description":"","filename":"4.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/c687185a696abe0d619ca914.png"},{"id":62731171,"identity":"217d4a2a-5bb3-4fdf-9fca-02f6cec2346b","added_by":"auto","created_at":"2024-08-18 23:28:52","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":796973,"visible":true,"origin":"","legend":"\u003cp\u003e(a) Lath distribution of the reference sample with no additional laser scan, (b) lath distribution of the fully post-heated sample, (c) single-scanned (only melting laser scan) regions of the ∅0.4 mm reinforcement application has lower lath angle compared to the (d) doubled-scanned regions. ∅0.6 mm reinforcement application has the same behavior (d) single-scanned regions have lower lath angle compared to the (e) double-scanned regions. On the contrary, (f) single-scanned regions have higher lath angle compared to double-scanned regions in ∅0.8 mm reinforcement application.\u003c/p\u003e","description":"","filename":"5.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/10ce72c41950c28ac5966bd6.png"},{"id":62731830,"identity":"c496fa2e-e2c6-4f80-bafc-9780cefb3c17","added_by":"auto","created_at":"2024-08-18 23:36:52","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":122581,"visible":true,"origin":"","legend":"\u003cp\u003eThe effect of the post-heating laser scan on HCP Lattice parameters; Sequential laser scan decreased the HCP lattice parameters “a” (a) and “c” (b). Post-heating laser scan increased the lattice distortion, c/a (c). The W-H model shows that the tension stress mode of the reference sample turned out to be a compression mode with the application of the post-heating laser scan (d).\u003c/p\u003e","description":"","filename":"6.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/f14ff5ac5b492f74d515c34a.png"},{"id":62731832,"identity":"1edc6b86-18a0-4e9c-a0f2-73931862ada4","added_by":"auto","created_at":"2024-08-18 23:36:52","extension":"png","order_by":7,"title":"Figure 7","display":"","copyAsset":false,"role":"figure","size":39971,"visible":true,"origin":"","legend":"\u003cp\u003eThe XRD patterns of the reference without additional laser scan and the post-heating laser scan specimens.\u003c/p\u003e","description":"","filename":"7.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/be6320baec3866189d868eb0.png"},{"id":62731178,"identity":"16790300-9a66-4ee2-9641-bf40143a9d77","added_by":"auto","created_at":"2024-08-18 23:28:53","extension":"png","order_by":8,"title":"Figure 8","display":"","copyAsset":false,"role":"figure","size":82893,"visible":true,"origin":"","legend":"\u003cp\u003e(a) Stress-strain curves for reference (black) and post-heating laser scan reinforcement applications. Each post-heating laser scan strategy, coupled with the specific reinforcement geometry, contributed to the enhanced strength of the LPBF-fabricated Ti-6Al-4V material. Notably, ∅0.6 mm reinforcement (yellow) demonstrated the most significant strength advancement. ∅0.4 mm (green) and ∅0.6 mm reinforcement (yellow) also enhanced the elongation extensively. However, fully post-heated (gray) and ∅0.8 mm reinforcement (blue) only enhanced the material’s strength. (b) Detailed values for the material elongation and strength are listed in the table.\u003c/p\u003e","description":"","filename":"8.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/a740adca0f6dc3ba03790dcc.png"},{"id":62732385,"identity":"7da31f56-5f35-4bcf-906d-80cfd7a64d32","added_by":"auto","created_at":"2024-08-18 23:44:53","extension":"png","order_by":9,"title":"Figure 9","display":"","copyAsset":false,"role":"figure","size":213972,"visible":true,"origin":"","legend":"\u003cp\u003eStrain before fracture DIC results of (a) reference as-built (b) fully post-heating laser scan application (c) ∅0.4 mm reinforcement (d) ∅0.6 mm reinforcement (e) ∅0.8 mm reinforcement application.\u003c/p\u003e","description":"","filename":"9.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/08e6579204a865b77e4393e5.png"},{"id":62731180,"identity":"1ecfaccb-5a22-4f32-a3d8-e040da14d9a7","added_by":"auto","created_at":"2024-08-18 23:28:53","extension":"png","order_by":10,"title":"Figure 10","display":"","copyAsset":false,"role":"figure","size":418037,"visible":true,"origin":"","legend":"\u003cp\u003ePhase transformation of the Ti-6Al-4V (a) β àα + β decomposition at a slower cooling rate ends up with relatively thicker α/α′ colonies. (b) β à α + β decomposition at a faster cooling rate starts with more random nucleation and ends up with relatively thinner α/α′ colonies.\u003c/p\u003e","description":"","filename":"10.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/5da3431322f9b961c96bb314.png"},{"id":62731181,"identity":"2d086178-47d7-497c-814c-2e54cde93cb5","added_by":"auto","created_at":"2024-08-18 23:28:53","extension":"png","order_by":11,"title":"Figure 11","display":"","copyAsset":false,"role":"figure","size":200893,"visible":true,"origin":"","legend":"\u003cp\u003eSuper-saturated HCP-Ti with the energy addition of the post-heating laser scan. Substitutional vanadium atoms occupied the titanium atom positions with the applied post-heating laser scan. Additionally, with additional laser scans oxygen atoms occupied the octahedral positions in the HCP-Ti.\u003c/p\u003e","description":"","filename":"11.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/2277cace66c70bc77fc93a51.png"},{"id":62731182,"identity":"8d6d49a9-5566-4221-9f1b-7b16dcee9dec","added_by":"auto","created_at":"2024-08-18 23:28:53","extension":"png","order_by":12,"title":"Figure 12","display":"","copyAsset":false,"role":"figure","size":48248,"visible":true,"origin":"","legend":"\u003cp\u003eThe general trend in the applied post-heating as HT after fabrication is a decrease in strength and an increase in elongation. The post-heating laser scan reinforcement application promises remarkable improvement in strength as well as elongation.\u003c/p\u003e","description":"","filename":"12.png","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/5f5d3a1b947b25575f16da0f.png"},{"id":72202046,"identity":"8c8aa104-deb7-416a-9531-3e3db52b841d","added_by":"auto","created_at":"2024-12-23 16:13:59","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":3867558,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-4751892/v1/71843b24-7d02-44b8-9ea8-e7bf5bf03175.pdf"}],"financialInterests":"","formattedTitle":"Single-Composition Functionally Graded Ti-6Al-4V for Mimicking Composite Material Fiber Reinforcement Through Post-Heating Laser Scanning","fulltext":[{"header":"1. Introduction","content":"\u003cp\u003eLPBF stands as one of the most common Additive Manufacturing (AM) techniques for metallic parts and has been captivating wide attention due to its fine feature resolution and superiorities in complex geometry fabrication. This led to the realization of bio-inspired [\u003cspan citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e] and lightweight component [\u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e] fabrication in the near-net shape without the necessity of machining. Additionally, LPBF helps to transform sub-assemblies into a single part, which decreases production costs and time [\u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eExceptional mechanical properties of the Ti-6Al-4V such as remarkable specific strength, excellent corrosion resistivity, biocompatibility, and superb fracture toughness explain its widespread use in aerospace [\u003cspan additionalcitationids=\"CR5\" citationid=\"CR4\" class=\"CitationRef\"\u003e4\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR6\" class=\"CitationRef\"\u003e6\u003c/span\u003e] and biomedical industries [\u003cspan additionalcitationids=\"CR8\" citationid=\"CR7\" class=\"CitationRef\"\u003e7\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e]. In addition, its adaptability to various manufacturing processes such as AM broadens its applications across various engineering industries.\u003c/p\u003e \u003cp\u003eLPBF fabrication capabilities and exceptional material properties of Ti-6Al-4V advanced the popularity of AM applications mostly in the aerospace industry [\u003cspan additionalcitationids=\"CR11\" citationid=\"CR10\" class=\"CitationRef\"\u003e10\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR12\" class=\"CitationRef\"\u003e12\u003c/span\u003e]. As a result of the increasing attention, the compelling combination of the LPBF process and the Ti-6Al-4V material has recently earned approval from the Federal Aviation Administration (FAA) for a flight critic component fabrication [\u003cspan citationid=\"CR13\" class=\"CitationRef\"\u003e13\u003c/span\u003e]. However, there is a certified application, microstructure complexity, and the anisotropic mechanical behavior of LPBF-fabricated Ti-6Al-4V are still not standardized. There are many studies in which the process and the material were comprehensively investigated, yet the challenges have not been fully addressed by researchers.\u003c/p\u003e \u003cp\u003eIn the LPBF technique, a high-power laser beam is precisely focused onto micron-sized areas. The focused laser beam interacts with the loose powder bed at extremely high scanning speeds, resulting in rapid solidification and cooling rates [\u003cspan citationid=\"CR14\" class=\"CitationRef\"\u003e14\u003c/span\u003e, \u003cspan citationid=\"CR15\" class=\"CitationRef\"\u003e15\u003c/span\u003e]. Thus, the LPBF technique leads to higher residual stresses in the part due to accelerated shrinkage and contraction arising from the processing method [\u003cspan citationid=\"CR16\" class=\"CitationRef\"\u003e16\u003c/span\u003e]. Additionally, the heat dissipation through the built material underneath the molten metal leads to directional cooling, resulting in a grain texture in the microstructure [\u003cspan additionalcitationids=\"CR18\" citationid=\"CR17\" class=\"CitationRef\"\u003e17\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e]. This induces anisotropy in the mechanical properties of the fabricated part which is directionally dependent. This directionally dependent mechanical response of the final part is considered an extensive problem that needs to be addressed [\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e, \u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e]. Some widely used approaches include changes in design and setting up the fabrication orientation which adds up to the production time and cost including the number of test qualifications required [\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eMaterials researchers have been studying this highly stressed and oriented microstructure to envision the impact of the fabrication process and explore novel methodologies for modifying its mechanical response. Post-heat treatment (HT) has been widely studied as a possible technique to modify the microstructure for desired improvements in mechanical response [\u003cspan additionalcitationids=\"CR24\" citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR25\" class=\"CitationRef\"\u003e25\u003c/span\u003e]. The impact of the various HTs on the LPBF-fabricated microstructure and its mechanical response has been studied comprehensively [\u003cspan additionalcitationids=\"CR27\" citationid=\"CR26\" class=\"CitationRef\"\u003e26\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR28\" class=\"CitationRef\"\u003e28\u003c/span\u003e]. Reports indicated an elongation improvement of up to 15.8% [\u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e] with a striking reduction in the strength of LPBF-fabricated Ti-6Al-4V [\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eAdditionally, materials researchers have applied different strengthening mechanisms to modify the complex microstructure and address the challenges related to the mechanical properties of the LPBF-fabricated Ti-6Al-4V material [\u003cspan additionalcitationids=\"CR31 CR32\" citationid=\"CR30\" class=\"CitationRef\"\u003e30\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR33\" class=\"CitationRef\"\u003e33\u003c/span\u003e]. One of the notable achievements reported was a 26.50% in the material\u0026rsquo;s strength with the addition of TiC particles to the melt pool of Ti-6Al-4V which resulted in a drastic reduction of the elongation [\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e]. It is coherent that there is an inverse relation between strengthening and plastic deformability.\u003c/p\u003e \u003cp\u003eIt was reported that the investigated complementary processes to modify the microstructure either enhanced the plastic deformation ability or the mechanical strength of the LPBF-fabricated Ti-6Al-4V. Here, a process-induced microstructure modification for the material\u0026rsquo;s reinforcement has been proposed and studied which enhanced the mechanical strength and plastic deformation ability for LPBF-fabricated Ti-6Al-4V. Although strength and plastic deformation are inversely proportional, results proved that with the studied innovative reinforcement approach it is possible to achieve remarkable improvement in strength along with a significant enhancement in elongation for LPBF-fabricated Ti-6Al-4V.\u003c/p\u003e \u003cp\u003ePrevious studies presented that it is possible to modify the LPBF-fabricated Ti-6Al-4V microstructure locally [\u003cspan additionalcitationids=\"CR36\" citationid=\"CR35\" class=\"CitationRef\"\u003e35\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR37\" class=\"CitationRef\"\u003e37\u003c/span\u003e] and fully [\u003cspan citationid=\"CR38\" class=\"CitationRef\"\u003e38\u003c/span\u003e] regarding the applied scanning strategy during the fabrication. In the present study, a post-heating laser scan was introduced upon the melting scan for the corresponding regions of the selected areas for each layer where the fiber texture of the composite materials was mimicked for reinforcement. The post-heating laser scan was studied at different laser power values and scan speeds to monitor the effect on microstructure. It was observed that optimized post-heating laser scan parameters have a significant effect on the inherent process-induced defects. The post-heating laser scan parameters that delivered the lowest porosity were assigned to the selected regions to modify the LPBF-fabricated Ti-6Al-4V material\u0026rsquo;s microstructure. The novel approach, which was inspired by the composite material\u0026rsquo;s nature, performed a tremendous strengthening in LPBF-fabricated Ti-6Al-4V material. Contrary to the common approaches in the literature, according to the results of the presented study, it is evident that the proposed in-situ strengthening enhances the strength along with the elongation of the material without the necessity of any complementary thermal processing or any additional compound during the fabrication.\u003c/p\u003e"},{"header":"2. Materials and Methods","content":"\u003cdiv id=\"Sec3\" class=\"Section2\"\u003e \u003ch2\u003e2.1 Materials\u003c/h2\u003e \u003cp\u003eTi-6Al-4V Grade 5 powder used for the fabrication was gas atomized and supplied by EOS North America (Pflugerville, TX, USA). The particle diameter of the powder ranged from 20 \u0026micro;m to 80 \u0026micro;m with a chemical composition of (wt.%) 5.50\u0026ndash;6.75 Al, 3.50\u0026ndash;4.50 V, 0.20 O, 0.05 N, 0.08 C, 0.015 H, 0.30 Fe, and the balance was Ti [\u003cspan citationid=\"CR39\" class=\"CitationRef\"\u003e39\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eMicrostructure samples fabricated with the dimensions of 20 mm \u0026times; 6 mm \u0026times; 6 mm and test coupons for tensile testing fabricated in dog-bone geometry with the dimensions and the applied regions exposed to the post-heating laser scan depicted in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e. The widely accepted tensile testing standard ASTM E8/E8M \u0026lsquo;Standard Test Methods for Tension Testing of Metallic Materials\u0026rsquo; does not have rectangular cross-section test specimen dimensions smaller than 25 mm gauge length. Thus, the authors designed a representative specimen geometry close to the standard dimension, which is suitable for multiple specimen fabrication in a single batch for the LPBF printer employed during the experimental study.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec4\" class=\"Section2\"\u003e \u003ch2\u003e2.2 Methods\u003c/h2\u003e \u003cp\u003eSamples were fabricated using Laser Powder Bed Fusion (LPBF) technology with an EOS M290 printer (EOS GmbH, Electro Optical Systems, Krailling, Germany) using Ytterbium fiber laser power of 400 W. To quantize the effect of the applied post-heating scan after melting the laser track, post-heating energy density was calculated from the energy density equation reported by Thijs \u003cem\u003eet al.\u003c/em\u003e (Eq.\u0026nbsp;\u003cspan refid=\"Equ1\" class=\"InternalRef\"\u003e1\u003c/span\u003e) [\u003cspan citationid=\"CR40\" class=\"CitationRef\"\u003e40\u003c/span\u003e].\u003cdiv id=\"Equ1\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ1\" name=\"EquationSource\"\u003e\n$$\\:{E}_{v}=\\frac{P}{v.h.t}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e1\u003c/div\u003e\u003c/div\u003e\u003c/p\u003e \u003cp\u003eCentral composite design (CCD) [\u003cspan citationid=\"CR41\" class=\"CitationRef\"\u003e41\u003c/span\u003e] was used for the post-heating laser scan process parameters in a variety of laser scan speeds between 650mm/s to 1950mm/s and laser power between 140W to 252W. In this design of experiment (DoE) 15 different variants were defined by the Box-Behnken method. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e illustrates the scanning sequences of the reference (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e (a)), layerwise post-heated (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e (b)), and layerwise locally post-heated applications (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e (c)).\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eThe suggested process parameters by the material supplier are 280 W laser power, 1300 mm/s scan speed, 120 \u0026micro;m hatch spacing, 100 \u0026micro;m laser spot size with a Gaussian distribution of energy, and 40 \u0026micro;m of layer thickness with 67\u0026deg; angle stripes scanning strategy [\u003cspan citationid=\"CR42\" class=\"CitationRef\"\u003e42\u003c/span\u003e]. These parameters were used for the melting laser scan on each layer initially and defined as the default parameters. Specimens were exposed first to the melting laser scan with default parameters and this was followed by a post-heating laser scan for the assigned regions of the tensile coupons. This scanning sequence was applied with variable post-heating energy densities (14.96 J/mm\u003csup\u003e3\u003c/sup\u003e to 80.77 J/mm\u003csup\u003e3\u003c/sup\u003e) to assess the microstructure response to the post-heating and investigate the mechanical properties of the final geometry. Scanning strategy, scanning pattern, layer thickness, hatch spacing, and hatch angle were kept at the value of suggested process parameters.\u003c/p\u003e \u003cp\u003eThe building plate temperature was preheated to 80 \u0026deg;C and maintained during the fabrication to reduce the thermal gradient of the first layer and delamination of the first layers. All specimens were cut from the building plate using a wire Electrical Discharge Machining (EDM) cutter (EDM Network, Inc., Sugar Grove, IL, USA).\u003c/p\u003e \u003cp\u003eScanning Electron Microscopy (SEM) imaging studies were performed for porosity, α-phase lath width, and grain morphology caused by various post-heating energy inputs. Samples were cut out by a TECHCUT 5\u0026trade; precision low-speed cutter (Allied High-Tech Products, Inc., Rancho Dominguez, CA, USA) from the center of the specimen along the building plane, prior to the sample preparation. Samples were cold mounted and prepared by grinding from 320 to 1200 grit size of SiC sandpaper. Afterward, the first step of polishing was performed on a DiaMat \u0026reg; polishing cloth with 1 \u0026micro;m diamond suspension. Polishing finalized with 0.04 \u0026micro;m colloidal silica suspension on Red Final C \u0026reg; polishing pad used to obtain scratch-free, mirror-like finish sample surfaces. Polished samples were rinsed in micro-organic soap and cleaned with isopropyl alcohol. Samples were etched with Kroll\u0026rsquo;s reagent (1\u0026ndash;3 mL HF, 2\u0026ndash;6 mL HNO\u003csub\u003e3\u003c/sub\u003e, 100 mL water) to identify the grain boundaries and phases of the microstructure.\u003c/p\u003e \u003cp\u003eImage J [\u003cspan citationid=\"CR43\" class=\"CitationRef\"\u003e43\u003c/span\u003e], an image analysis software, was used to calculate the porosity level of each microstructure. The porosity distribution was determined from at least three different regions at 2 magnification levels (500x and 1000x). Image J was also used for the lath width calculation of the α-phase. For image processing, microstructure images were first converted to RGB stack-type grayscale images prior to setting the auto contrast level. Thresholding was generated to create a clear contrast between α/α\u0026prime; phases\u0026rsquo; lath borders. Particles were analyzed between 0.2 \u0026micro;m to 2.0 \u0026micro;m then total counts of the particle at each size were calculated for the mean value. This calculation made at least 6 different images for statistically meaningful data from every sample\u0026rsquo;s building plane orientation.\u003c/p\u003e \u003cp\u003eX-ray diffraction analyses were performed for phase identification, calculation of the lattice parameters, and orientations of the microstructure of each sample. A Bruker D8 Advance X-ray diffractometer (Bruker Corporation, Madison, WI, USA) was used for the analysis with 1.5406 \u0026Aring; Cu k-alpha wavelength, 40 mA current, 40 kV voltage at room temperature, and the measurements were taken with step intervals of 0.5\u0026deg; and a scan speed of 1sec/step while the 2θ varied between 20\u0026deg; to 80\u0026deg;.\u003c/p\u003e \u003cp\u003eLattice parameters were calculated according to Bragg\u0026rsquo;s law (Eq.\u0026nbsp;(\u003cspan refid=\"Equ2\" class=\"InternalRef\"\u003e2\u003c/span\u003e)) where d, is inter-planar spacing, a and c are the lattice parameters and h, k, l are the Miller indices.\u003cdiv id=\"Equ2\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ2\" name=\"EquationSource\"\u003e\n$$\\:\\frac{1}{{d}^{2}}=\\:\\frac{4}{3}\\:\\left(\\frac{{h}^{2}+hk+\\:{k}^{2}}{{a}^{2}}\\:\\right)+\\:\\frac{{l}^{2}}{{c}^{2}}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e2\u003c/div\u003e\u003c/div\u003e\u003cdiv id=\"Equa\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equa\" name=\"EquationSource\"\u003e\n$$\\:\\lambda\\:=2d\\:sinϴ$$\u003c/div\u003e\u003c/div\u003e\u003c/p\u003e \u003cp\u003eThe Williamson \u0026ndash; Hall (W\u0026ndash;H) model [\u003cspan citationid=\"CR44\" class=\"CitationRef\"\u003e44\u003c/span\u003e] was employed to assess the microstrain condition of the microstructure of the reference and post-heating laser scan application. The XRD data was utilized in the following equations (Eq.\u0026nbsp;(3) (4) (5)). Peak broadening of the XRD data is caused by crystal imperfections and distortion which is related by ε\u0026thinsp;\u0026asymp;\u0026thinsp;βs / tanθ. The W\u0026ndash;H plot was used for the calculation of the microstrain value. Si standard reflection (0.0013 rad) [\u003cspan citationid=\"CR45\" class=\"CitationRef\"\u003e45\u003c/span\u003e] was subtracted before strain analysis using W\u0026ndash;H method. The Scherrer\u0026rsquo;s equation (Eq.\u0026nbsp;(3)) derived to Eq.\u0026nbsp;(5) where β is peak broadening, λ is the wavelength (\u0026Aring;). K is the Cu Ks (0.94), D is the crystallite size (nm) and θ is the peak position.\u003c/p\u003e \u003cp\u003eD = \u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\frac{\\lambda\\:\\:K}{\\beta\\:\\:cos\\theta\\:}\\)\u003c/span\u003e\u003c/span\u003e (3)\u003c/p\u003e \u003cp\u003eβ = \u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\sqrt{{{\\beta\\:}_{T}}^{2}-\\:{{\\beta\\:}_{i}}^{2}}\\)\u003c/span\u003e\u003c/span\u003e (4)\u003c/p\u003e \u003cp\u003eβ cosθ = \u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\frac{\\lambda\\:\\:K}{D}\\)\u003c/span\u003e\u003c/span\u003e + 4ε sinθ (5)\u003c/p\u003e \u003cp\u003eShimadzu EHF E-Series (100kN) equipped with a 4830-servo controller (Shimadzu Scientific Instruments, Inc., Missouri City, TX, USA) was used for tensile testing. Strain measurements of the gauge region were made by using a digital image correlation (DIC) system. The surface strain and displacements were captured by tracking the patterns of the high-contrast speckles on the coupon surface. This contactless technique can measure the local strains at the fracture as well as the global strain during the loading of the coupons. Two 2.3MP CCD cameras, Grasshopper GS3-U3-23S6M (FLIR Systems, Inc., Santa Barbra, CA, USA) with a pixel array of 1920 x 1200 were used for image capturing. Processing of the captured images and correlation with the stress loading were made using VIC-3D\u0026reg; software (Correlated Solutions, Inc., Irmo, SC, USA). Considering the previous studies [\u003cspan citationid=\"CR46\" class=\"CitationRef\"\u003e46\u003c/span\u003e, \u003cspan citationid=\"CR47\" class=\"CitationRef\"\u003e47\u003c/span\u003e], the loading rate was set to 1.2 mm/min for all tests.\u003c/p\u003e \u003c/div\u003e"},{"header":"3. Results","content":"\u003cdiv id=\"Sec6\" class=\"Section2\"\u003e\n \u003ch2\u003e3.1 Microstructure\u003c/h2\u003e\n \u003cdiv id=\"Sec7\" class=\"Section3\"\u003e\n \u003ch2\u003e3.1.1 Defect / Porosity Analysis\u003c/h2\u003e\n \u003cp\u003eThe porosity levels corresponding to the selected post-heating laser power values and post-heating laser scan speeds were studied using the Box-Behnken DoE model. A total of fifteen post-heating laser power and scan speed variations were characterized and their effect on porosity was evaluated. SEM micrographs at various regions and magnification levels for each scenario revealed that the post-heating laser scan significantly impacted the inherent porosity level of L-PBF Ti-6Al-4V. The RSM plot for the post-heating laser power between 140\u0026ndash;252W and post-heating laser scan speed between 650\u0026ndash;1950 mm/s was depicted in Fig. \u003cspan class=\"InternalRef\"\u003e3\u003c/span\u003e (a). It was confirmed that 650 mm/s post-heating laser scan speed delivered the minimum porosity levels for each post-heating laser scan power. Additionally, it was observed the post-heating laser power of 140W minimized the porosity during the experimental study. The relation between the post-heating laser scan speed and the porosity level of the microstructure at the constant post-heating laser scan power (140 W) was depicted in Fig. \u003cspan class=\"InternalRef\"\u003e3\u003c/span\u003e (b). The porosity level of the reference sample without a complemental post-heating laser scan was measured at 0.47% \u0026plusmn; 0.015 [\u003cspan class=\"CitationRef\"\u003e47\u003c/span\u003e]. It was undoubted that a subsequent laser scan decreased the initial porosity level, and it was measured to be up to 90%. The denser microstructure of the post-laser scan can be ascribed to remelting [\u003cspan class=\"CitationRef\"\u003e48\u003c/span\u003e, \u003cspan class=\"CitationRef\"\u003e49\u003c/span\u003e]. The inherent porosity level of the L-PBF Ti-6Al-4V was minimized with the post-heating laser scan parameters of 140W laser power and 650mm/s laser scan speed. These optimized parameters delivered almost a fully dense (\u0026gt;\u0026thinsp;99.95%) microstructure and were subjected to further microstructural and mechanical testing as the post-heating laser scan sample and selected for the post-heating laser applications of the presented study. The microstructure response after the post-heating laser scan for circular reinforcement regions of diameters \u0026empty;0.4 mm, \u0026empty;0.6 mm, and \u0026empty;0.8 mm was illustrated in Fig. \u003cspan class=\"InternalRef\"\u003e3\u003c/span\u003e (c), and the porosity levels were measured as 0.08\u0026thinsp;\u0026plusmn;\u0026thinsp;0.01%, 0.07\u0026thinsp;\u0026plusmn;\u0026thinsp;0.06%, 0.07\u0026thinsp;\u0026plusmn;\u0026thinsp;0.07%, respectively.\u003c/p\u003e\n \u003cp\u003e\u0026nbsp;\u003c/p\u003e\n \u003c/div\u003e\n \u003cdiv id=\"Sec8\" class=\"Section3\"\u003e\n \u003ch2\u003e3.1.2 Grain Morphology and Lattice Structure\u003c/h2\u003e\n \u003cp\u003eThe microstructure of the Ti-6Al-4V, an \u0026alpha;\u0026thinsp;+\u0026thinsp;\u0026beta; alloy, fabricated via LPBF consists of a greater number of \u0026alpha;/\u0026alpha;\u0026prime; phases at room temperature, which exhibits a basketweave-like structure [\u003cspan class=\"CitationRef\"\u003e50\u003c/span\u003e]. The lath width of the basketweave-like structure determines the mechanical response of the alloy [\u003cspan class=\"CitationRef\"\u003e51\u003c/span\u003e]. The grain morphology of the Ti-6Al-4V alloy was assessed, and the response of the \u0026alpha;/\u0026alpha;\u0026prime; phases\u0026rsquo; lath structure to the applied processes was evaluated. Table\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e1\u003c/span\u003e depicts the average lath width and the lath angle for each application. The average lath width of the samples was measured with image processing[\u003cspan class=\"CitationRef\"\u003e43\u003c/span\u003e] of the SEM micrographs at magnification levels of 500x, 800x, 1200x, and 1500x. The lath width of the reference sample was measured to be 0.797\u0026thinsp;\u0026plusmn;\u0026thinsp;0.005 \u0026micro;m. The highest lath width was observed in the microstructure samples which were fully exposed to the optimized post-heating laser scan (0.894\u0026thinsp;\u0026plusmn;\u0026thinsp;0.051 \u0026micro;m). The lowest lath width was observed in the double-scanned regions of the \u0026empty;0.4 mm reinforcement application (0.687\u0026thinsp;\u0026plusmn;\u0026thinsp;0.007). It was evident that an additional post-heating laser scan across the entire cross-section of the samples had a significant effect on lath width. Results showed a 12% increase in the lath width between the reference (no additional laser scan) and the sample fully exposed to the post-heating laser scan. The variation in lath width between the single and double-scanned regions in the microstructure of reinforcement applications was also evaluated. The limited application of the post-heating laser scan only to the projection of the reinforcement geometries on the samples\u0026rsquo; cross-section did not have a major effect compared to the fully applied post-heating laser to the samples\u0026rsquo; cross-section. The highest variation was observed in the \u0026empty;0.8 mm reinforcement application and calculated as a 3.6% increase with the addition of a post-heating laser scan.\u003c/p\u003e\n \u003cdiv class=\"gridtable\"\u003e\n \u003cdiv class=\"colspec\" align=\"left\"\u003e\u0026nbsp;\u003c/div\u003e\n \u003cdiv class=\"colspec\" align=\"char\"\u003e\u0026nbsp;\u003c/div\u003e\n \u003ctable id=\"Tab1\" border=\"1\"\u003e\n \u003ccaption\u003e\n \u003cdiv class=\"CaptionNumber\"\u003eTable 1\u003c/div\u003e\n \u003cdiv class=\"CaptionContent\"\u003e\n \u003cp\u003eHCP \u0026ndash; Ti (\u0026alpha;/\u0026alpha;\u0026prime; phases) lath width and angle.\u003c/p\u003e\n \u003c/div\u003e\n \u003c/caption\u003e\n \u003cthead\u003e\n \u003ctr\u003e\n \u003cth align=\"left\"\u003e\u0026nbsp;\u003c/th\u003e\n \u003cth align=\"left\"\u003e\n \u003cp\u003eReference\u003c/p\u003e\n \u003cp\u003e(No additional laser scan)\u003c/p\u003e\n \u003c/th\u003e\n \u003cth align=\"left\"\u003e\n \u003cp\u003eFully Post-heated\u003c/p\u003e\n \u003c/th\u003e\n \u003cth colspan=\"2\" align=\"left\"\u003e\n \u003cp\u003e\u0026empty;0.4mm Reinforcement Scan\u003c/p\u003e\n \u003c/th\u003e\n \u003cth colspan=\"2\" align=\"left\"\u003e\n \u003cp\u003e\u0026empty;0.6mm Reinforcement Scan\u003c/p\u003e\n \u003c/th\u003e\n \u003cth colspan=\"2\" align=\"left\"\u003e\n \u003cp\u003e\u0026empty;0.8mm Reinforcement Scan\u003c/p\u003e\n \u003c/th\u003e\n \u003c/tr\u003e\n \u003c/thead\u003e\n \u003ctbody\u003e\n \u003ctr\u003e\n \u003ctd align=\"left\"\u003e\u0026nbsp;\u003c/td\u003e\n \u003ctd align=\"left\"\u003e\u0026nbsp;\u003c/td\u003e\n \u003ctd align=\"left\"\u003e\u0026nbsp;\u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting Scan\u003c/p\u003e\n \u003cp\u003e(single scan region)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting\u0026thinsp;+\u0026thinsp;Post-heating Scan (double scan region)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting Scan\u003c/p\u003e\n \u003cp\u003e(single laser region)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting\u0026thinsp;+\u0026thinsp;Post-heating Scan (double laser region)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting Scan\u003c/p\u003e\n \u003cp\u003e(single laser region)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eMelting\u0026thinsp;+\u0026thinsp;Post-heating Scan (double laser scan)\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eAve. Lath Width (\u0026micro;m)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"char\"\u003e\n \u003cp\u003e0.797\u0026thinsp;\u0026plusmn;\u0026thinsp;0.005\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"char\"\u003e\n \u003cp\u003e0.894\u0026thinsp;\u0026plusmn;\u0026thinsp;0.051\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.691\u0026thinsp;\u0026plusmn;\u0026thinsp;0.006\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.687\u0026thinsp;\u0026plusmn;\u0026thinsp;0.007\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.749\u0026thinsp;\u0026plusmn;\u0026thinsp;0.007\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.727\u0026thinsp;\u0026plusmn;\u0026thinsp;0.006\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.690\u0026thinsp;\u0026plusmn;\u0026thinsp;0.010\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e0.715\u0026thinsp;\u0026plusmn;\u0026thinsp;0.005\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003eAve. Lath Angle (\u0026deg;)\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"char\"\u003e\n \u003cp\u003e118.08\u0026thinsp;\u0026plusmn;\u0026thinsp;2.69\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"char\"\u003e\n \u003cp\u003e81.88\u0026thinsp;\u0026plusmn;\u0026thinsp;7.27\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e95.13\u0026thinsp;\u0026plusmn;\u0026thinsp;3.77\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e98.38\u0026thinsp;\u0026plusmn;\u0026thinsp;3.07\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e95.20\u0026thinsp;\u0026plusmn;\u0026thinsp;1.99\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e98.00\u0026thinsp;\u0026plusmn;\u0026thinsp;1.85\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e98.19\u0026thinsp;\u0026plusmn;\u0026thinsp;0.81\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd align=\"left\"\u003e\n \u003cp\u003e94.36\u0026thinsp;\u0026plusmn;\u0026thinsp;1.32\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003c/tbody\u003e\n \u003c/table\u003e\n \u003c/div\u003e\n \u003cp\u003eLath structure micrograph images of the \u0026alpha;/\u0026alpha;\u0026prime; phases of each application are shown in Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e4\u003c/span\u003e. The representative images of the microstructure variation between the single-scan and double-scanned regions (projection of the reinforcement geometries on the cross-section) for \u0026empty;0.4, \u0026empty;0.6, and \u0026empty;0.8 mm reinforcement application is illustrated in Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e4\u003c/span\u003e (c), (d), and (e) respectively. The lath width slightly decreased in the double-scanned scan regions for \u0026empty;0.4 mm and \u0026empty;0.6 mm reinforcement size. In opposition, the lath width was measured thicker in \u0026empty;0.8 mm reinforcement size at the double scanned regions.\u003c/p\u003e\n \u003cp\u003eIn addition to size, the angle of the \u0026alpha;-colonies affects the deformation mechanism and the strength of the Ti-6Al-4V alloy [\u003cspan class=\"CitationRef\"\u003e52\u003c/span\u003e]. The lath angle of the \u0026alpha;/\u0026alpha;\u0026prime; phases was analyzed with image processing [\u003cspan class=\"CitationRef\"\u003e43\u003c/span\u003e]. The lath angles with respect to their width have been presented in Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e5\u003c/span\u003e. Lath sizes between the range of 0 to 2 \u0026micro;m have been plotted with their corresponding angles. It was observed that almost all the laths concentrated themselves either within 0\u0026ordm; and 75\u0026ordm; or between 75\u0026ordm; and 180\u0026ordm;. The lath densities in the measured window is found to be higher in the double exposed region than in the single exposed region as seen from Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e5\u003c/span\u003e. This phenomenon was observed with all other reinforcement sizes tested.\u003c/p\u003e\n \u003cp\u003eThe investigated grain morphology of the \u0026alpha;/\u0026alpha;\u0026prime; phases have a hexagonal close-packed (HCP) lattice structure. Lattice parameters HCP structure of the \u0026alpha;/\u0026alpha;\u0026prime; phases were calculated according to Bragg\u0026rsquo;s law [\u003cspan class=\"CitationRef\"\u003e53\u003c/span\u003e] and plotted in Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e6\u003c/span\u003e. A reduction in both lattice parameters of a and c was observed (Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e6\u003c/span\u003e (a) and (b)). Additionally, a strain on the lattice was observed with the applied post-heating laser scan. Figure\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e6\u003c/span\u003e (c) shows the strain with a higher c/a ratio with the additional laser scan. The post-heating laser scan increased the c/a ratio of the lattice which is a result of the lower cooling rate [\u003cspan class=\"CitationRef\"\u003e54\u003c/span\u003e] of the post-heating laser scan application.\u003c/p\u003e\n \u003cp\u003eThe W-H model was employed for further microstructure analysis to gain a better understanding of the strain and stress condition of the samples. Eq.\u0026nbsp;(5) was considered as a y\u0026thinsp;=\u0026thinsp;mx\u0026thinsp;+\u0026thinsp;c equation and the equation was plotted as the W-H model in which the slope of this equation is the microstrain value [\u003cspan class=\"CitationRef\"\u003e44\u003c/span\u003e]. According to the model, the initial microstrain condition of the microstructure at the reference sample without a complementary post-heating laser scan was determined as tension. The positive slope of the plotted model of the reference sample is shown in red in Fig.\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e6\u003c/span\u003e (d). A remarkable change in the initial condition of the L-PBF Ti-6Al-4V was observed after the application of the post-heating laser scan. The plotted model of the post-heating laser scan shows a negative slope which indicates that the microstrain condition of the microstructure was turned out in compression mode. The effect of the tension and compression mode of the microstructure on the mechanical response will be discussed in the discussion section.\u003c/p\u003e\n \u003c/div\u003e\n\u003c/div\u003e\n\u003cdiv id=\"Sec9\" class=\"Section2\"\u003e\n \u003ch2\u003e3.2 Compositional Analysis XRD\u003c/h2\u003e\n \u003cp\u003eFigure \u003cspan class=\"InternalRef\"\u003e7\u003c/span\u003e depicts the XRD profiles of the reference and post-heated specimens. The highest intensity of Bragg\u0026rsquo;s peak was observed at the (101) plane on the XY plane of the reference sample. Despite the post-heating samples have similar peak patterns, it is noteworthy that the strongest peak intensity was observed at the (002) plane on the XY plane. The remarkable change in the peak intensities indicated that the majority of the grain orientation was modified with the applied post-heating laser scan along the (002) plane.\u003c/p\u003e\n\u003c/div\u003e\n\u003cdiv id=\"Sec10\" class=\"Section2\"\u003e\n \u003ch2\u003e3.3 Mechanical Testing\u003c/h2\u003e\n \u003cp\u003eThe mechanical response of the modified microstructure was quantified through tensile testing. The stress-strain plot is depicted in Fig.\u0026nbsp;8. The post-heating laser scan reinforcement strategy had a significant effect on the mechanical response of the material. It was observed that both ultimate tensile strength (UTS) and yield strength (YS) values were enhanced. A remarkable increase in the slope during elastic deformation led to a higher YS for each post-heating laser scan strategy applied in the present study. The enhancements in YS were 22.6%, 11.4%, 46.5%, and 34.6% for the reinforcement applications of fully post-heating, \u0026empty;0.4 mm, \u0026empty;0.6 mm, and \u0026empty;0.8 mm reinforcement size, respectively. The \u0026empty;0.6 mm reinforcement delivered an extensive advancement in UTS with a strength value of 1608\u0026thinsp;\u0026plusmn;\u0026thinsp;122 MPa. This is followed by \u0026empty;0.8 mm reinforcement, fully post-heated application, and \u0026empty;0.4 mm reinforcement with the strength values of 1485\u0026thinsp;\u0026plusmn;\u0026thinsp;91 MPa, 1335\u0026thinsp;\u0026plusmn;\u0026thinsp;96 MPa, 1217\u0026thinsp;\u0026plusmn;\u0026thinsp;44 MPa, respectively. Reinforcement geometries of \u0026empty;0.4 mm and \u0026empty;0.6 mm delivered exceptional elongations, which were 69.0% and 99.3% higher compared to the reference sample, respectively. On the contrary \u0026empty;0.8 mm reinforcement coupons and the fully post-heating coupons ended up with a slightly lower elongation compared to the reference sample.\u003c/p\u003e\n \u003cp\u003e\u0026nbsp;\u003c/p\u003e\n \u003cp\u003eIt was observed that the applied post-heating laser strategy changed the deformation during the tensile testing. Figure\u0026nbsp;\u003cspan class=\"InternalRef\"\u003e9\u003c/span\u003e depicts the DIC results of localized plastic deformation before fracture for each application. Results show that applied post-heating laser scan regardless the geometry of the scanning area, modified the deformation behavior of the LPBF-fabricated Ti-6Al-4V. Local deformation accumulated in various angles and locations after the application of the post-heating laser scan.\u003c/p\u003e\n \u003cp\u003e\u0026nbsp;\u003c/p\u003e\n\u003c/div\u003e"},{"header":"4. Discussions","content":"\u003cp\u003eIn the present study, an in-situ strengthening strategy during the LPBF process for Ti-6Al-4V was evaluated. A post-heating laser scan was employed upon the melting scan to maximize the relative density and modify the Ti-6Al-4V material\u0026rsquo;s microstructure in terms of α/α\u0026prime; phases (HCP-Ti) grain and lattice structure. Furthermore, the complementary post-heating laser scans aimed to enhance the inherent grain texture of the LPBF-fabricated Ti-6Al-4V through directional solidification and cooling. The post-heating laser scan was applied both fully across the microstructure and only to the designated regions in the specimens\u0026rsquo; cross-section. The fiber structure of the composite materials was replicated in the presented study, and reinforcement geometries with different diameters were assigned into the samples as the reinforcements during the design process and a building file was generated for the scan strategy for each application accordingly. The projection of these geometries onto the cross-section of the coupons was exposed to an additional post-heating laser scan which parameters minimized the inherent porosity value. The preliminary data of the microstructure, which was fully exposed to the post-heating laser scan, clearly indicated a strengthening effect. It is rational to observe a reduction in the material\u0026rsquo;s elongation for the strengthened materials [\u003cspan citationid=\"CR55\" class=\"CitationRef\"\u003e55\u003c/span\u003e]. With this strategy, \u0026sim;50% of the cross-section was aimed at strengthening, thus the reduction in the elongation would be limited compared to the fully post-heated sample. Results proved that the reinforcement strategy presented in this study improved the elongation significantly whereas the LPBF fabricated Ti-6Al-4V delivered higher strength compared to previous thermal processing studies.\u003c/p\u003e \u003cdiv id=\"Sec12\" class=\"Section2\"\u003e \u003ch2\u003e4.1 Localized Post-heating Laser Scan Effect on Process-induced Defects\u003c/h2\u003e \u003cp\u003eThe impact of the post-heating laser scan parameters (laser power (W), laser scan speed (mm/s)) on the process-induced porosity can be seen in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e. (a). The figure provides significant insights regarding the correlation between post-heating laser scan parameters, such as laser power and scanning speed, and their impact on reducing the porosity level. It was observed the post-heating laser scan power of 140W and scanning speed of 650 mm/s delivered the lowest porosity level. Post-heating laser scan with 140W laser power and 650 mm/s scanning speed decreased the porosity level from 0.470\u0026ndash;0.046%. Additionally, results indicated that the lowest porosity value for different post-heating laser powers (252W and 196W) was delivered with a scanning speed of 650 mm/s (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e (b)). A similar effect was reported in re-melting studies with higher energy inputs to the powder bed[\u003cspan additionalcitationids=\"CR57\" citationid=\"CR56\" class=\"CitationRef\"\u003e56\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR58\" class=\"CitationRef\"\u003e58\u003c/span\u003e] and Hot Isostatic Pressure (HIP) applications in which additional processing was required [\u003cspan citationid=\"CR59\" class=\"CitationRef\"\u003e59\u003c/span\u003e, \u003cspan citationid=\"CR60\" class=\"CitationRef\"\u003e60\u003c/span\u003e].\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec13\" class=\"Section2\"\u003e \u003ch2\u003e4.2 α/α\u0026prime; Phase Lath Structure Tailoring by Localized Post-heating Laser Scan\u003c/h2\u003e \u003cp\u003eThe predominant stable phases in the LPBF-fabricated Ti-6Al-4V microstructure at room temperature were observed as α and α\u0026prime; phases. Due to the complexity of the LPBF fabricated Ti-6Al-4V alloy\u0026rsquo;s microstructure it requires additional microstructure characterization tools to distinguish these phases from each other which is not the scope of the presented study. It has been a common practice in the literature to evaluate the microstructure of LPBF-fabricated Ti-6Al-4V alloy for its mechanical properties together as the α/α\u0026prime; phases, α-Ti or HCP-Ti [\u003cspan citationid=\"CR61\" class=\"CitationRef\"\u003e61\u003c/span\u003e]. The difference between these phases depends on the cooling rate and their structure is distinct from each other due to the lath width. The higher cooling rate delivers a thinner lath width which is called as martensite and annotated as α\u0026prime; phase, and the relatively slower cooling regions are α phases with a pattern called Widmanst\u0026auml;tten [\u003cspan citationid=\"CR62\" class=\"CitationRef\"\u003e62\u003c/span\u003e]. It is rational to examine both phases together since the average lath width was considered for the microstructure investigation. In addition, both phases have an HCP lattice structure, which cannot be distinguished when computing the lattice parameters using XRD data. The impact of the post-heating laser scan on α-Ti lath width is listed in Table\u0026nbsp;\u003cspan refid=\"Tab1\" class=\"InternalRef\"\u003e1\u003c/span\u003e. The application of the post-heating laser scan fully across the microstructure increased the average lath width of the material. A comparable effect was observed with the conventional HTs, however, the observed lath coarsening after the applied post-heating laser scan (12.17% increase) was below the reported HT applications; Zou \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR63\" class=\"CitationRef\"\u003e63\u003c/span\u003e] applied heat treatment to L-PBF Ti-6Al-4V below the β-transus temperature (925\u0026deg;C/2hr/FC(7\u0026deg;C/min)) and authors reported a 40% increase on lath width, Lu \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR64\" class=\"CitationRef\"\u003e64\u003c/span\u003e] applied a heat treatment above the β-transus temperature (1015\u0026deg;C/1hr/AC) and a 75% increase on lath width was reported. In addition to these conventional post-heat treatments, Karami \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR65\" class=\"CitationRef\"\u003e65\u003c/span\u003e] reported a \u0026sim;110% increase with the application of hot isostatic processing (HIP) HIP (920\u0026deg;C/2hr/100MPa).\u003c/p\u003e \u003cp\u003e \u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab2\" border=\"1\"\u003e \u003ccaption language=\"En\"\u003e \u003cdiv class=\"CaptionNumber\"\u003eTable 2\u003c/div\u003e \u003cdiv class=\"CaptionContent\"\u003e \u003cp\u003eEffect of the post-HT on the mechanical behavior of the L-PBF Ti-6Al-4V\u003c/p\u003e \u003c/div\u003e \u003c/caption\u003e \u003ccolgroup cols=\"9\"\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c5\" colnum=\"5\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c6\" colnum=\"6\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c7\" colnum=\"7\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c8\" colnum=\"8\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c9\" colnum=\"9\"\u003e\u003c/div\u003e \u003cthead\u003e \u003ctr\u003e \u003cth align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/th\u003e \u003cth align=\"left\" colname=\"c2\"\u003e \u003cp\u003eHeat Treatment\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c3\"\u003e \u003cp\u003eYS As-Built (MPa)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c4\"\u003e \u003cp\u003eYS HTed (MPa)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c5\"\u003e \u003cp\u003eAs-Built Elongation (%)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c6\"\u003e \u003cp\u003eHTed Elongation (%)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c7\"\u003e \u003cp\u003eChange of YS (%)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c8\"\u003e \u003cp\u003eChange of Elongation (%)\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/th\u003e \u003c/tr\u003e \u003c/thead\u003e \u003ctbody\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eEtesami \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR66\" class=\"CitationRef\"\u003e66\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e900\u0026deg;/2hr/AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e\u0026sim;1180\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026sim;1100\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e8.7\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e4.9\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-6.77\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e-43.67\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eSimonelli \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR67\" class=\"CitationRef\"\u003e67\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e730\u0026deg;C/2h/FC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1075\u0026thinsp;\u0026plusmn;\u0026thinsp;25(H)\u003c/p\u003e \u003cp\u003e967\u0026thinsp;\u0026plusmn;\u0026thinsp;10(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e974\u0026thinsp;\u0026plusmn;\u0026thinsp;7(H)\u003c/p\u003e \u003cp\u003e937\u0026thinsp;\u0026plusmn;\u0026thinsp;7(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.6\u0026thinsp;\u0026plusmn;\u0026thinsp;0.5(H)\u003c/p\u003e \u003cp\u003e8.9\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e7.0\u0026thinsp;\u0026plusmn;\u0026thinsp;0.5(H)\u003c/p\u003e \u003cp\u003e9.6\u0026thinsp;\u0026plusmn;\u0026thinsp;0.9(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-9.39\u003c/p\u003e \u003cp\u003e-3.10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e-8.57\u003c/p\u003e \u003cp\u003e7.86\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eVilaro \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR68\" class=\"CitationRef\"\u003e68\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003eSupersolvus\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1137\u0026thinsp;\u0026plusmn;\u0026thinsp;20(H)\u003c/p\u003e \u003cp\u003e962\u0026thinsp;\u0026plusmn;\u0026thinsp;47(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e913\u0026thinsp;\u0026plusmn;\u0026thinsp;7(H)\u003c/p\u003e \u003cp\u003e836\u0026thinsp;\u0026plusmn;\u0026thinsp;64(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.6\u0026thinsp;\u0026plusmn;\u0026thinsp;2(H)\u003c/p\u003e \u003cp\u003e1.7\u0026thinsp;\u0026plusmn;\u0026thinsp;0.3(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e8.9\u0026thinsp;\u0026plusmn;\u0026thinsp;1(H)\u003c/p\u003e \u003cp\u003e7.9\u0026thinsp;\u0026plusmn;\u0026thinsp;1(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-19.70\u003c/p\u003e \u003cp\u003e-13.09\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e17.11\u003c/p\u003e \u003cp\u003e364.7\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003eSubtransus\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1137\u0026thinsp;\u0026plusmn;\u0026thinsp;20(H)\u003c/p\u003e \u003cp\u003e962\u0026thinsp;\u0026plusmn;\u0026thinsp;47(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e944\u0026thinsp;\u0026plusmn;\u0026thinsp;8(H)\u003c/p\u003e \u003cp\u003e925\u0026thinsp;\u0026plusmn;\u0026thinsp;14(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.6\u0026thinsp;\u0026plusmn;\u0026thinsp;2(H)\u003c/p\u003e \u003cp\u003e1.7\u0026thinsp;\u0026plusmn;\u0026thinsp;0.3(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e8.5\u0026thinsp;\u0026plusmn;\u0026thinsp;1(H)\u003c/p\u003e \u003cp\u003e7.5\u0026thinsp;\u0026plusmn;\u0026thinsp;2(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-19.70\u003c/p\u003e \u003cp\u003e-3.84\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e11.84\u003c/p\u003e \u003cp\u003e341.1\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003eLow Temperature\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1137\u0026thinsp;\u0026plusmn;\u0026thinsp;20(H)\u003c/p\u003e \u003cp\u003e962\u0026thinsp;\u0026plusmn;\u0026thinsp;47(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e965\u0026thinsp;\u0026plusmn;\u0026thinsp;16(H)\u003c/p\u003e \u003cp\u003e900\u0026thinsp;\u0026plusmn;\u0026thinsp;101(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.6\u0026thinsp;\u0026plusmn;\u0026thinsp;2(H)\u003c/p\u003e \u003cp\u003e1.7\u0026thinsp;\u0026plusmn;\u0026thinsp;0.3(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e9.5\u0026thinsp;\u0026plusmn;\u0026thinsp;1(H)\u003c/p\u003e \u003cp\u003e1.9\u0026thinsp;\u0026plusmn;\u0026thinsp;0.8(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-15.12\u003c/p\u003e \u003cp\u003e-6.44\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e25.00\u003c/p\u003e \u003cp\u003e11.76\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eVrancken \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR69\" class=\"CitationRef\"\u003e69\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e540\u0026deg;C/5hr/WQ\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1110\u0026thinsp;\u0026plusmn;\u0026thinsp;9\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e1118\u0026thinsp;\u0026plusmn;\u0026thinsp;39\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.28\u0026thinsp;\u0026plusmn;\u0026thinsp;1.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e5.36\u0026thinsp;\u0026plusmn;\u0026thinsp;2.02\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e0.72\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e-26.37\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e1020\u0026deg;C /2hr/FC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1110\u0026thinsp;\u0026plusmn;\u0026thinsp;9\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e760\u0026thinsp;\u0026plusmn;\u0026thinsp;19\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.28\u0026thinsp;\u0026plusmn;\u0026thinsp;1.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e14.06\u0026thinsp;\u0026plusmn;\u0026thinsp;2.53\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-31.53\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e93.13\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e850\u0026deg;C/5hr/FC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1110\u0026thinsp;\u0026plusmn;\u0026thinsp;9\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e909\u0026thinsp;\u0026plusmn;\u0026thinsp;6\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.28\u0026thinsp;\u0026plusmn;\u0026thinsp;1.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003ePremature failure\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-18.10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003eN/A\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e1050\u0026deg;C/0.5hr/AC\u0026thinsp;+\u0026thinsp;730\u0026deg;C/2hr/AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1110\u0026thinsp;\u0026plusmn;\u0026thinsp;9\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e822\u0026thinsp;\u0026plusmn;\u0026thinsp;19\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7.28\u0026thinsp;\u0026plusmn;\u0026thinsp;1.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e12.74\u0026thinsp;\u0026plusmn;\u0026thinsp;0.56\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-25.94\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e75.00\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eCao \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR70\" class=\"CitationRef\"\u003e70\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e800\u0026deg;C/2hr\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e\u0026sim;1020(H)\u003c/p\u003e \u003cp\u003e\u0026sim;950(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026sim;950(H)\u003c/p\u003e \u003cp\u003e\u0026sim;850(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e\u0026sim;4\u003c/p\u003e \u003cp\u003e\u0026sim;4\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e\u0026sim;9\u003c/p\u003e \u003cp\u003e\u0026sim;6\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-6.86\u003c/p\u003e \u003cp\u003e-10.52\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e125.00\u003c/p\u003e \u003cp\u003e50.00\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eSabban \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR71\" class=\"CitationRef\"\u003e71\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e975\u0026deg;C \u0026minus;\u0026thinsp;875\u0026deg;C\u003c/p\u003e \u003cp\u003e(Cyclic HT)\u003c/p\u003e \u003cp\u003e/24hr/AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1047\u0026thinsp;\u0026plusmn;\u0026thinsp;23(H)\u003c/p\u003e \u003cp\u003e1043\u0026thinsp;\u0026plusmn;\u0026thinsp;18(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e865\u0026thinsp;\u0026plusmn;\u0026thinsp;19(H)\u003c/p\u003e \u003cp\u003e849\u0026thinsp;\u0026plusmn;\u0026thinsp;12(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e10\u0026thinsp;\u0026plusmn;\u0026thinsp;1(H)\u003c/p\u003e \u003cp\u003e12\u0026thinsp;\u0026plusmn;\u0026thinsp;1(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e18\u0026thinsp;\u0026plusmn;\u0026thinsp;1(H)\u003c/p\u003e \u003cp\u003e16\u0026thinsp;\u0026plusmn;\u0026thinsp;1(V)\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-17.38\u003c/p\u003e \u003cp\u003e-18.60\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e80.00\u003c/p\u003e \u003cp\u003e33.33\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eZhang \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR72\" class=\"CitationRef\"\u003e72\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e900\u0026deg;C/6hr/AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1112\u0026thinsp;\u0026plusmn;\u0026thinsp;8\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e864\u0026thinsp;\u0026plusmn;\u0026thinsp;3\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e7\u0026thinsp;\u0026plusmn;\u0026thinsp;1\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e10\u0026thinsp;\u0026plusmn;\u0026thinsp;1\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-22.30\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e42.86\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e750\u0026deg;C/2hr/FC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1351\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e1185\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e3.14\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e3.4\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-12.29\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e8.28\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eYan \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR73\" class=\"CitationRef\"\u003e73\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e800\u0026deg;C/2hr/FC\u0026thinsp;+\u0026thinsp;AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1065\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e996\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e6\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e7\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-6.47\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e16.67\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e1080\u0026deg;C/2hr/FC\u0026thinsp;+\u0026thinsp;AC\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1065\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e840\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e6\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e4\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e-21.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e-33.33\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eKasperovich \u003cem\u003eet al.\u003c/em\u003e [\u003cspan citationid=\"CR74\" class=\"CitationRef\"\u003e74\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e900\u0026deg;C/2hr\u0026thinsp;+\u0026thinsp;700\u0026deg;C/1hr\u003c/p\u003e \u003cp\u003e/FC(10K/min)\u003c/p\u003e \u003cp\u003eAnnealed\u003c/p\u003e \u003cp\u003e600\u0026deg;C\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e986\u003c/p\u003e \u003cp\u003e990\u0026thinsp;\u0026plusmn;\u0026thinsp;5\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e908\u003c/p\u003e \u003cp\u003e870\u0026thinsp;\u0026plusmn;\u0026thinsp;15\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e11.9\u003c/p\u003e \u003cp\u003e8.1\u0026thinsp;\u0026plusmn;\u0026thinsp;0.3\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e9.5\u003c/p\u003e \u003cp\u003e11.0\u0026thinsp;\u0026plusmn;\u0026thinsp;0.5\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e-7.91\u003c/p\u003e \u003cp\u003e-12.12\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\" morerows=\"1\" rowspan=\"2\"\u003e \u003cp\u003e-20.17\u003c/p\u003e \u003cp\u003e35.80\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eFacchini \u003cem\u003eet al\u003c/em\u003e.[\u003cspan citationid=\"CR75\" class=\"CitationRef\"\u003e75\u003c/span\u003e]\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eFully Post Heating Laser Scan\u003c/p\u003e \u003cp\u003e\u0026empty;0.4 mm Reinforcement\u003c/p\u003e \u003cp\u003ePost Heating \u003c/p\u003e \u003cp\u003eLaser Scan\u003c/p\u003e \u003cp\u003e\u0026empty;0.6 mm Reinforcement\u003c/p\u003e \u003cp\u003ePost Heating \u003c/p\u003e \u003cp\u003eLaser Scan\u003c/p\u003e \u003cp\u003e\u0026empty;0.8 mm Reinforcement\u003c/p\u003e \u003cp\u003ePost Heating \u003c/p\u003e \u003cp\u003eLaser Scan\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e-\u003c/p\u003e \u003cp\u003e-\u003c/p\u003e \u003cp\u003e-\u003c/p\u003e \u003cp\u003e-\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e1001\u0026thinsp;\u0026plusmn;\u0026thinsp;38\u003c/p\u003e \u003cp\u003e1001\u0026thinsp;\u0026plusmn;\u0026thinsp;38\u003c/p\u003e \u003cp\u003e1001\u0026thinsp;\u0026plusmn;\u0026thinsp;38\u003c/p\u003e \u003cp\u003e1001\u0026thinsp;\u0026plusmn;\u0026thinsp;38\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e1228\u0026thinsp;\u0026plusmn;\u0026thinsp;80\u003c/p\u003e \u003cp\u003e1115\u0026thinsp;\u0026plusmn;\u0026thinsp;44\u003c/p\u003e \u003cp\u003e1467\u0026thinsp;\u0026plusmn;\u0026thinsp;85\u003c/p\u003e \u003cp\u003e1347\u0026thinsp;\u0026plusmn;\u0026thinsp;62\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e3.26\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4\u003c/p\u003e \u003cp\u003e3.26\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4\u003c/p\u003e \u003cp\u003e3.26\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4\u003c/p\u003e \u003cp\u003e3.26\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e4.28\u0026thinsp;\u0026plusmn;\u0026thinsp;0.4\u003c/p\u003e \u003cp\u003e5.51\u0026thinsp;\u0026plusmn;\u0026thinsp;0.2\u003c/p\u003e \u003cp\u003e6.50\u0026thinsp;\u0026plusmn;\u0026thinsp;0.7\u003c/p\u003e \u003cp\u003e4.11\u0026thinsp;\u0026plusmn;\u0026thinsp;0.2\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e22.6\u003c/p\u003e \u003cp\u003e11.4\u003c/p\u003e \u003cp\u003e46.5\u003c/p\u003e \u003cp\u003e34.6\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e31.3\u003c/p\u003e \u003cp\u003e69.0\u003c/p\u003e \u003cp\u003e99.3\u003c/p\u003e \u003cp\u003e26.1\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colspan=\"1\" nameend=\"c9\" namest=\"c9\"\u003e\u0026nbsp;\u003c/td\u003e \u003c/tr\u003e \u003c/tbody\u003e \u003c/colgroup\u003e \u003c/table\u003e\u003c/div\u003e \u003c/p\u003e \u003cp\u003eα/α\u0026prime; lath colonies decompose from the β-grain boundaries during the phase transformation below the allotropic transformation temperature. The cooling rate during the phase transformation defines the nucleation and grain growth of the precipitate phase. Faster cooling rates resulted in thinner laths with more randomly distributed structures since α/α\u0026prime; nucleation starts irregularly inner side of the β-grain as well as the β-grain boundaries [\u003cspan citationid=\"CR50\" class=\"CitationRef\"\u003e50\u003c/span\u003e]. A schematic view of the α/α\u0026prime; lath colonies formation is depicted in Fig.\u0026nbsp;\u003cspan refid=\"Fig9\" class=\"InternalRef\"\u003e10\u003c/span\u003e.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eA slight decrease in the lath thickness of the α/α\u0026prime; colonies was observed in the double-scanned regions of the \u0026empty;0.4 mm and \u0026empty;0.6 mm reinforcement applications. Authors considered this as a result of different cooling compared to the single scanned regions where microstructure inhomogeneity is higher due to the rapid and directional cooling [\u003cspan citationid=\"CR76\" class=\"CitationRef\"\u003e76\u003c/span\u003e, \u003cspan citationid=\"CR77\" class=\"CitationRef\"\u003e77\u003c/span\u003e]. The effective thermal conductivity of the Ti-6Al-4V powder bed during the melting scan is 0.13 W/mK [\u003cspan citationid=\"CR78\" class=\"CitationRef\"\u003e78\u003c/span\u003e] which is much less compared to the bulk Ti-6Al-4V. Findings revealed a linear relation between the temperature of the Ti-6Al-4V and its thermal conductivity, according to the study presented by Saini \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR79\" class=\"CitationRef\"\u003e79\u003c/span\u003e] thermal conductivity of Ti-6Al-4V exceeds 20 W/mK at 1200\u0026deg;C. This value is almost 154 times higher than the thermal conductivity of the loose powder. The complementary post-heating process applied the high-temperature solidified Ti-6Al-4V material which has relatively higher thermal conductivity and led to a faster cooling rate and delivered thinner α/α\u0026prime; colonies (Table\u0026nbsp;\u003cspan refid=\"Tab1\" class=\"InternalRef\"\u003e1\u003c/span\u003e). The reinforcement application of the \u0026empty;0.8 mm had a different response which will be evaluated in future studies.\u003c/p\u003e \u003cp\u003eThe angle at which the laths align themselves gives us an idea of the homogeneity in microstructure formation and thus the strength of the resulting part [\u003cspan citationid=\"CR80\" class=\"CitationRef\"\u003e80\u003c/span\u003e]. In-homogeneity in the grain orientations is one of the primary sources of dislocation sites from where the crack initiates before leading to failure upon mechanical loading. Figure\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e. helps us comment on the grain orientations observed in the reinforcement regions compared to non-reinforcement regions. Looking at the lath density concentrations, grain orientation homogeneity seems to improve within the reinforcement regions. This highlights that the resulting solid part comprises homogeneous and in-homogeneous grain orientations. It should also be noted that as the reinforcement size reduced, the largely variant lath densities in the reinforcement region when compared to the non-reinforcement regions seem to be reduced. This might be because of the fact that the volume of material receiving the higher energy density has a direct correlation to its effect on the lath formation in the neighboring regions. Bigger reinforcements transfer higher thermal energy to the non-processed regions thus making the entire region of a cross-section with uniformly orienting laths.\u003c/p\u003e \u003cp\u003eThe lath width of the α/α\u0026prime; phase had a significant effect on the mechanical response of the L-PBF Ti-6Al-4V material [\u003cspan citationid=\"CR66\" class=\"CitationRef\"\u003e66\u003c/span\u003e, \u003cspan citationid=\"CR81\" class=\"CitationRef\"\u003e81\u003c/span\u003e]. Hadadzadeh \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR81\" class=\"CitationRef\"\u003e81\u003c/span\u003e] attributed the high strength of L-PBF Ti-6Al-4V to finer α/α\u0026prime; laths through the Hall-Petch effect[\u003cspan citationid=\"CR82\" class=\"CitationRef\"\u003e82\u003c/span\u003e] and Etesami \u003cem\u003eet al\u003c/em\u003e[\u003cspan citationid=\"CR66\" class=\"CitationRef\"\u003e66\u003c/span\u003e] reported the remarkable effect of the α/α\u0026prime; laths width on elongation during the tensile test. In the present study, lath coarsening was observed, and it is one of the reasons for the preferred elongation.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec14\" class=\"Section2\"\u003e \u003ch2\u003e4.3 Localized Post-heating Laser Scan Effect on Crystallography\u003c/h2\u003e \u003cp\u003eThe findings, as depicted in Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e, demonstrated the post-heating laser scan has a remarkable effect on the LPBF-fabricated Ti-6Al-4V lattice structure as well as the microstrain. An increase in the lattice parameters was reported in previous studies[\u003cspan citationid=\"CR83\" class=\"CitationRef\"\u003e83\u003c/span\u003e, \u003cspan citationid=\"CR84\" class=\"CitationRef\"\u003e84\u003c/span\u003e] with the application of the post-heat treatment. The increase in the lattice parameters was attributed to the higher diffusivity of the vanadium atoms[\u003cspan citationid=\"CR84\" class=\"CitationRef\"\u003e84\u003c/span\u003e, \u003cspan citationid=\"CR85\" class=\"CitationRef\"\u003e85\u003c/span\u003e] of Ti-6Al-4V during the post-heat treatment temperatures. Vanadium atoms diffused out of the HCP lattice and larger titanium atoms[\u003cspan citationid=\"CR86\" class=\"CitationRef\"\u003e86\u003c/span\u003e] occupied their positions which transformed the structure into a larger lattice. On the contrary to the conventional post-heat treatment applications, a slight decrease in the lattice parameters both a and c was observed with the application of the post-heating laser scan (Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e (a) \u0026amp; (b)). Lattice shrinkage can be explained by the vanadium atoms diffusion mechanism. It is well-known that additional heat leads to an increase in temperature which improves the solubility of the substitutional atoms in this case of the post-heating laser scan application it is vanadium atoms [\u003cspan citationid=\"CR87\" class=\"CitationRef\"\u003e87\u003c/span\u003e]. The increasing amount of the substitutional vanadium atoms leads to a decrease in the lattice parameters since vanadium has smaller atomic radii compared to titanium atoms that were substituted by vanadium during the post-heating laser scan. Compared to the conventional HTs, the post-heating laser scan exhibits a relatively higher cooling rate. The smaller lattice parameters of the post-heating laser scan can be rationalized with faster cooling rates with lower diffusivity, which limits the diffusion of the excessive vanadium atoms from their positions inside the HCP lattice.\u003c/p\u003e \u003cp\u003eThe previous study demonstrated that introducing additional laser scan to the powder bed exceeds the operation temperature, causing an increase in the affinity of titanium to oxygen [\u003cspan citationid=\"CR47\" class=\"CitationRef\"\u003e47\u003c/span\u003e]. This makes the molten metal more sensitive to oxidation, even under shield gas protection. The lattice strain measured in the presented study (Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e) can be justified by the same phenomenon. Figure\u0026nbsp;\u003cspan refid=\"Fig10\" class=\"InternalRef\"\u003e11\u003c/span\u003e depicts the representative image of the super-saturated HCP lattice with the octahedral position occupied by the oxygen atoms which strains the lattice along the c-axis. Addition to the lattice strain Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e depicts the decrease in both a and c lattice parameters, result of the trapped vanadium atoms in the HCP lattice which occupies the titanium atom positions with smaller atomic radii. It is known that the lattice distortion due to the interstitial oxygen atoms strengthens the LPBF-fabricated Ti-6Al-4V material [\u003cspan citationid=\"CR47\" class=\"CitationRef\"\u003e47\u003c/span\u003e, \u003cspan citationid=\"CR88\" class=\"CitationRef\"\u003e88\u003c/span\u003e].\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec15\" class=\"Section2\"\u003e \u003ch2\u003e4.4 Mechanical Response of the Material to the Reinforcement by Localized Post-heating\u003c/h2\u003e \u003cp\u003eThe resulting tensile strength and elongation on the reinforcement applications have been studied (Fig.\u0026nbsp;8.) It was observed that post-heating through a second laser scan resulted in a remarkable enhancement in the material\u0026rsquo;s strength. It is rational to have a lower elongation with the increase in strength after the strengthening process [\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e]. This is noticeable when the post-heating laser scan was applied fully across the cross-section of the material (Fig.\u0026nbsp;8. (a) gray line). Considering that, when the post-heating laser was carried out in limited localized regions (circular area of the reinforcement geometry projection on the sample cross-section), there seems to be a significant increase in the elongation along with tensile strength for the 0.4 mm and 0.6 mm reinforcement diameter (Fig.\u0026nbsp;8. (a) green and yellow line). It is interesting to note that the highest elongation was observed for the 0.6 mm reinforcement size reinforcements which also had the highest tensile strength among all the test cases. This fascinating occurrence of obtaining higher strength and higher elongation can be explained by the reinforcement matrix formation due to the combination of finer and coarser α/α\u0026prime; lath regions obtained within the cross-section of a solidified Ti6Al4 microstructure. It further helped to direct research attention toward identifying the limits at which the matrix strengthening occurs depending on the reinforced area of the post-heated section. It should also be noted that the shape of the region that is being post-heated might influence the properties as well which need to be further investigated.\u003c/p\u003e \u003cp\u003eThe common practice of strengthening in the literature has been studied by introducing additional elements and components to the microstructure of the LPBF-fabricated Ti-6Al-4V such as nitrogen, and titanium-carbide. Liu \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR89\" class=\"CitationRef\"\u003e89\u003c/span\u003e] investigated the in-situ nitrogen strengthening of the LPBF-fabricated Ti-6Al-4V by introducing nitrogen to the build chamber through the shield gas. The highest improvement in the YS was reported as 20.01% with a drastic reduction in elongation. However, the authors reported a significant improvement in the material\u0026rsquo;s strength, the elongation of the strengthened material was decreased by almost half of the initial condition. He \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR90\" class=\"CitationRef\"\u003e90\u003c/span\u003e] studied the strengthening of the Ti-6Al-4V with the addition of LaB\u003csub\u003e6\u003c/sub\u003e to the LPBF process. In their study, the highest improvement in the material\u0026rsquo;s strength was 14.50% with a 37.2% reduction in elongation. TiC addition to the Ti-6Al-4V components during the LPBF process is also a preferred way to reinforce the material [\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e, \u003cspan citationid=\"CR91\" class=\"CitationRef\"\u003e91\u003c/span\u003e]. Jiang \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR91\" class=\"CitationRef\"\u003e91\u003c/span\u003e] investigated the effect of TiC in Ti-6Al-4V during the LPBF process and the authors reported titanium matrix composites with TiC addition had a 10.68% higher strength with a very limited elongation. Tang \u003cem\u003eet al.\u003c/em\u003e[\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e] in their TiC reinforcement study, it was reported that the highest improvement in strength was \u0026sim;26.50% with an elongation of 3.65% which is less than half of the initial as-built condition of the material. Previous studies have revealed that the strengthening of LPBF fabricated Ti-6Al-4V was limited to \u0026sim;26.50% and caused a notable reduction in elongation. The proposed innovative reinforcement strategy of post-heating laser scan was assigned to designated regions on the specimen. It was observed that the studied reinforcement strategy of post-heating laser scan resulted in a remarkable improvement of \u0026sim;50% in YS which is the highest enhancement in the strength among the previously reported studies. More importantly, a remarkable improvement in the elongation (\u0026sim;100% improvement) was also achieved with the proposed composite additive manufacturing application for the first time. Thus, the elongation reduction due to the strengthening is promised to be controlled as well as improved for the engineering applications.\u003c/p\u003e \u003cp\u003ePost-heating HT is one of the most popular complementary processes that was applied to modify the microstructure of the LPBF-fabricated Ti-6Al-4V. Table\u0026nbsp;\u003cspan refid=\"Tab2\" class=\"InternalRef\"\u003e2\u003c/span\u003e depicts the mechanical response of the modified microstructure after the HT. However, there are some studies that reported a decrease both in strength and elongation, the general response after HT was a decrease in the strength and an increase in elongation. It is due to the lath coarsening and the stress relieving effect of the HT which is discussed previously. The studied post-heating laser scan strategy modified the LPBF Ti-6Al-4V microstructure by reforming the α/α\u0026prime; phases lath structure (Table\u0026nbsp;\u003cspan refid=\"Tab1\" class=\"InternalRef\"\u003e1\u003c/span\u003e. and Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e.), HCP lattice structure (Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e.), initial microstrain mode (Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e.) and the grain texture (Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e7\u003c/span\u003e.). Figure\u0026nbsp;\u003cspan refid=\"Fig11\" class=\"InternalRef\"\u003e12\u003c/span\u003e depicts the yield strength and the elongation of the LPBF fabricated Ti-6Al-4V material after conventional HT and the post-heating laser scan reinforcement application (green region). Considering the studies listed in Table\u0026nbsp;\u003cspan refid=\"Tab2\" class=\"InternalRef\"\u003e2\u003c/span\u003e and Fig.\u0026nbsp;8. the proposed reinforcement application that mimicked the composite materials with a complementary post-heating laser scan of the limited regions of the cross-section during the fabrication promised to dismiss the thermal post-processing of LPBF fabricated Ti-6Al-4V with superior mechanical properties.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eA notable enhancement in YS was observed for each reinforcement application, attributed to the modification of the α/α\u0026prime; colonies by localized post-heating laser scan and eliminated process-induced defects (Fig.\u0026nbsp;8). Compared to the reference sample each post-heating application had higher yielding point. It is known that the grain boundary network with respect to the population and connectivity enhances the polycrystalline materials [\u003cspan citationid=\"CR92\" class=\"CitationRef\"\u003e92\u003c/span\u003e]. At further deformation, modified grain boundary crystallography impacts the dislocation motion[\u003cspan citationid=\"CR93\" class=\"CitationRef\"\u003e93\u003c/span\u003e] which was observed in the present study with higher UTS values during the tensile testing (Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e7\u003c/span\u003e).\u003c/p\u003e \u003c/div\u003e"},{"header":"5. Conclusion","content":"\u003cp\u003eThe present study proposed an innovative strengthening strategy for the LPBF process by mimicking the fiber texture of the composite materials. The reinforcement shape was selected to replicate the fiber function of reinforcement in the matrix. Different reinforcement diameters were selected according to the resolution of the LPBF technology to study the effect of reinforcement size on the mechanical response of the material. The corresponding regions of the assigned reinforcement shape at each layer were exposed to a secondary laser scan through the sample during the fabrication.\u003c/p\u003e \u003cp\u003eStudied microstructure clearly demonstrated that the optimized post-heating laser scan modified the LPBF-fabricated Ti-6Al-4V alloy\u0026rsquo;s microstructure by recrystallizing the α/α\u0026prime; phases lath structure, stretching the HCP lattice, transforming the initial strain mode, and the inherent grain texture.\u003c/p\u003e \u003cp\u003eNotably, the mechanical response of the tailored microstructure for reinforcement indicated a remarkable improvement in strength. The post-heating laser scan reinforcement application was observed to increase elongation, as well as the strength of the material for each reinforcement diameter.\u003c/p\u003e \u003cp\u003eThe results apparently indicated that the proposed innovative thermal processing of the LPBF-fabricated Ti-6Al-4V during the fabrication can alternate the requirement of the complementary post-processing of heat treatment to modify the microstructure for the desired mechanical response. Additionally, results promised to strengthen the material without the requirement of auxiliary components such as nitrides, or carbides which makes the LPBF process more challenging in non-uniform chemical composition distribution.\u003c/p\u003e"},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eFunding:\u0026nbsp;\u003c/strong\u003ethis research received no external funding\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eConflict of interest\u003c/strong\u003e: The authors declare no conflicts of interest\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAuthors\u0026rsquo; Contribution: Ahmet Alptug Tanrikulu\u003c/strong\u003e: Conceptualization, writing-original-draft, characterization, methodology. \u003cstrong\u003eAditya Krishna Ganesh-Ram\u003c/strong\u003e: writing-review-editing, testing, investigation, fabrication. \u003cstrong\u003eHamidreza Hekmatjou\u003c/strong\u003e: investigation, data analysis, pre-processing. \u003cstrong\u003eSadman Hafiz Durlov:\u0026nbsp;\u003c/strong\u003ewriting-review-editing, theoretical investigation.\u003cstrong\u003e\u0026nbsp;Amirhesam Amerinatanzi\u003c/strong\u003e: Resources, supervision, conceptualization, writing-review-editing.\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\u003cli\u003e\u003cspan\u003eYang J, Gu D, Lin K et al (2022) Laser Additive Manufacturing of Bio-inspired Metallic Structures. 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Mater Sci Engineering: A 243:32\u0026ndash;45. \u003cspan class=\"ExternalRef\"\u003e\u003cspan class=\"RefSource\"\u003ehttps://doi.org/10.1016/S0921-5093(97)00778-8\u003c/span\u003e\u003cspan address=\"10.1016/S0921-5093(97)00778-8\" targettype=\"DOI\" class=\"RefTarget\"\u003e\u003c/span\u003e\u003c/span\u003e\u003c/span\u003e\u003c/li\u003e\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":false,"highlight":"","institution":"","isAcceptedByJournal":true,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"the-international-journal-of-advanced-manufacturing-technology","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"jamt","sideBox":"Learn more about [The International Journal of Advanced Manufacturing Technology](https://www.springer.com/journal/170)","snPcode":"170","submissionUrl":"https://submission.nature.com/new-submission/170/3","title":"The International Journal of Advanced Manufacturing Technology","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"em","reportingPortfolio":"Springer Hybrid","inReviewEnabled":true,"inReviewRevisionsEnabled":false},"keywords":"Functionally graded microstructure, LPBF, Ti-6Al-4V, in situ microstructure modification, post-heating laser scan, multiple laser scan","lastPublishedDoi":"10.21203/rs.3.rs-4751892/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-4751892/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eProcess-induced microstructure modification was investigated for the strengthening mechanism of Laser Powder Bed Fusion Fabricated (LPBF) Ti-6Al-4V material. An innovative approach by mimicking the fiber structure of the composite materials was studied. Different cylindrical reinforcement diameters were selected in the LPBF-fabricated Ti-6Al-4V samples to replicate the function of the carbon fibers in composite materials, providing stiffness and reinforcement in the matrix. The corresponding regions of the assigned Reinforcement shape at each layer were exposed to a secondary laser scan through the sample during the fabrication. Multi-scan laser scanning strategies, involving a combination of laser power and scan speed were employed after the melting laser scan to maximize the relative density of the material. The optimized post-heating laser scan enhanced the relative density (\u0026gt;\u0026thinsp;99.95%), recrystallized the α and α\u0026prime; phases\u0026rsquo; lath morphology, modified the lattice structure, transformed the initial microstrain mode, and enhanced the inherent grain texture of the PBF fabricated Ti-6Al-4V. The tailored microstructure achieved a 46.5% higher yield strength (YS) accompanied by a 99.3% higher elongation.\u003c/p\u003e","manuscriptTitle":"Single-Composition Functionally Graded Ti-6Al-4V for Mimicking Composite Material Fiber Reinforcement Through Post-Heating Laser Scanning","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2024-08-18 23:28:47","doi":"10.21203/rs.3.rs-4751892/v1","editorialEvents":[{"type":"communityComments","content":0},{"type":"decision","content":"Minor Revisions Needed","date":"2024-11-22T14:15:04+00:00","index":"","fulltext":""},{"type":"reviewerAgreed","content":"","date":"2024-07-27T19:14:41+00:00","index":0,"fulltext":""},{"type":"reviewersInvited","content":"","date":"2024-07-20T14:14:56+00:00","index":"","fulltext":""},{"type":"editorAssigned","content":"","date":"2024-07-19T01:45:27+00:00","index":"","fulltext":""},{"type":"submitted","content":"The International Journal of Advanced Manufacturing Technology","date":"2024-07-18T02:17:40+00:00","index":"","fulltext":""}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"the-international-journal-of-advanced-manufacturing-technology","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"jamt","sideBox":"Learn more about [The International Journal of Advanced Manufacturing Technology](https://www.springer.com/journal/170)","snPcode":"170","submissionUrl":"https://submission.nature.com/new-submission/170/3","title":"The International Journal of Advanced Manufacturing Technology","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"em","reportingPortfolio":"Springer Hybrid","inReviewEnabled":true,"inReviewRevisionsEnabled":false}}],"origin":"","ownerIdentity":"0a7d2484-8526-4d88-a5f3-c06699b61835","owner":[],"postedDate":"August 18th, 2024","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"published-in-journal","subjectAreas":[],"tags":[],"updatedAt":"2024-12-23T16:07:23+00:00","versionOfRecord":{"articleIdentity":"rs-4751892","link":"https://doi.org/10.1007/s00170-024-14902-z","journal":{"identity":"the-international-journal-of-advanced-manufacturing-technology","isVorOnly":false,"title":"The International Journal of Advanced Manufacturing Technology"},"publishedOn":"2024-12-19 15:57:36","publishedOnDateReadable":"December 19th, 2024"},"versionCreatedAt":"2024-08-18 23:28:47","video":"","vorDoi":"10.1007/s00170-024-14902-z","vorDoiUrl":"https://doi.org/10.1007/s00170-024-14902-z","workflowStages":[]},"version":"v1","identity":"rs-4751892","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-4751892","identity":"rs-4751892","version":["v1"]},"buildId":"qtupq5eGEP_6zYnWcrvyt","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}