## 4 Conclusions  
The quasi-static mechanical properties of various microstructures of LPBF Ti6 Al4V(ELI) were presented and discussed in this study, with the following conclusions deduced:  
1. The orientation of samples C and D consisted of several invariants of \(\alpha\)-grains related to \(\beta\!\!\rightarrow\!\!\alpha\) phase transformation during cooling. The orientation map of samples E consisted of semi-equiaxed and equiaxed shapes of the prior \(\beta\) grains with various colonies, each consisting of crystals with similar orientation.
2. The \(\alpha\)-laths in colonies of most semi-equiaxed and equiaxed \(\beta\)-grains in samples E possessed LAGBs between them and HAGBs between different colonies.
3. About 50% and 45% of the EBSD-scanned areas in samples C and D were occupied by grains, with individual areas being \(\leq\) 5 um\({}^{2}\) and \(\leq\) 38 um\({}^{2}\), respectively. About 38% of the EBSD-scanned area in samples E was occupied by large grains with areas between 14,830 um\({}^{2}\) and 35,090 um\({}^{2}\).  
\begin{table}
\begin{tabular}{c c c c c} \hline \hline  & & & & \\ \hline
**Test Strain Rate** & **Samples C** & **Samples D** & **Samples E** & **Reference** \\ \hline
0.001 s\({}^{-1}\) & 2 μm & 4 μm & 5 μm & Present study \\
0.005 s\({}^{-1}\) & 2 μm & 5 μm & 5 μm & Present study \\
0.1 s\({}^{-1}\) & 3 μm & 7 μm & 5 μm & Present study \\
750 s\({}^{-1}\) & 3 μm & 12.3 μm & 12.4 μm & [45] \\
1500 s\({}^{-1}\) & 5 μm & 14.7 μm & 18.4 μm & [45] \\ \hline \hline \end{tabular}
\end{table}
Table 3: The thickness of ASBs in samples C, D and E for tests conducted at quasi-static and high strain rates.  
* About 66%, 63% and 43% of \(\alpha\)-grains in samples C, D and E, respectively, had their global Schmid factor higher at values in the range of 0.4-0.5 for the basal slip system in the direction of application of quasi-static load.
* The values of yield and flow stresses for the three different microstructures of LPBF Ti6 Al4V(ELI) increased with an increase in quasi-static strain rate.
* The order of the strength of the different forms of LPBF Ti6 Al4V(ELI) from the highest to the lowest at different strain rates was seen to be samples C, D and E.
* Various microstructures of LPBF Ti6 Al4V(ELI) exhibited noticeable flow hardening at different levels of strain rate for the larger part of the flow stress curve.
* The effects of strain rate on flow hardening were significant in samples C and insignificant in samples D and E.
* Adiabatic shear bands were the primary failure mechanism in the three different forms of the DMLS Ti6 Al4V(ELI) alloy.  
Conceptualization, A.M., M.M. and W.d.P.; methodology, A.M.; formal analysis, A.M.; writing--original draft preparation, A.M.; writing--review and editing, A.M., M.M. and W.d.P.; supervision, M.M. and W.d.P.; funding acquisition, W.d.P. and M.M. All authors have read and agreed to the published version of the manuscript.  
This research was funded by the South African Department of Science and Innovation (DSI) through the Council for Scientific and Industrial Research (CSIR), for the Collaborative Program in Additive Manufacturing, Contract No.: CSIR -NLC-CPAM-21-MOA-CUT-01.  
Not applicable.  
The datasets presented in this study are available on request from the corresponding author and are not publicly available as they form part of ongoing research.  
The authors acknowledge the Centre for Rapid Prototyping and Manufacturing (CRPM) of the Central University of Technology, Free State (CUT) for production of test specimens used for this study. The Centre for High Resolution Transmission Electron Microscopy (CHRTEM) of the Nelson Mandela University where the EBSD analyses were carried out is acknowledged. The authors also express their gratitude to the mechanical engineering laboratory of the Council for Scientific and Industrial Research (CSIR) of South Africa, where quasi-static experiments were conducted.  
The authors declare no conflict of interest.