## 2 Materials and Methods
[24], it is shown that alloys of a Fe-Cr-C system with a different B4C content were successfully deposited on the surface of stainless steel, for instance, AISI 316, via plasma-arc welding. The coating microstructure was predominantly a \(\gamma\)-Fe,Ni eutectic matrix, and hexagonal carbides (Cr, Fe)\({}_{7}\)(C,B)\({}_{3}\) and (Cr, Fe)\({}_{23}\)(C,B)\({}_{6}\) were not uniformly distributed in the eutectic matrix. The average microhardness of the deposited coating was equal to 820 HV, which was almost five times higher than that of the substrate from AISI 316 stainless steel (180 HV). The maximal value of the coating microhardness was close to 1280 HV. Such structural features of the deposited coatings can considerably influence the stress-strain state of the produced layers. \begin{table}
\begin{tabular}{c c c c c c c c} \hline \hline \multirow{2}{*}{**Spectrum**} & \multicolumn{6}{c}{**Element Content, wt. \%**} \\ \cline{2-7}  & **B** & **O** & **Si** & **Cr** & **Mn** & **Fe** & **Ni** \\ \hline
1 & 5.57 & 2.79 & 1.51 & 17.33 & 0.28 & 65.21 & 7 \\ \hline
2 & 6.19 & 2.68 & 1.41 & 17.34 & 0.37 & 64.8 & 7.08 \\ \hline
3 & 6 & 2.98 & 1.47 & 17.48 & 0.23 & 65.06 & 6.61 \\ \hline
4 & 6.69 & 2.65 & 1.42 & 17.81 & 0.45 & 64.88 & 6.11 \\ \hline
5 & 3.6 & 1.83 & 1.46 & 17 & 0.38 & 67.2 & 8.53 \\ \hline
6 & 4.43 & 2.94 & 1.17 & 15.6 & 0.2 & 66.79 & 8.86 \\ \hline
7 & 2.65 & 3.97 & 2.04 & 15.68 & 0.3 & 67.07 & 8.29 \\ \hline
8 & 5.97 & – & 1.16 & 17.05 & 0.15 & 66.75 & 8.92 \\ \hline
9 & 3.33 & 1.43 & 1.25 & 17.41 & 0.24 & 71.81 & 4.29 \\ \hline
10 & 2 & 1.98 & 1.55 & 17.09 & 0.33 & 68.07 & 8.85 \\ \hline \hline \end{tabular}
\end{table} 
Table 2: Chemical composition of the particles of HYF–103 powder according to the data gathered via scanning electron microscopy. Figure 1: Morphology of initial HYF–103 powder: (**a**)—appearance and chemical composition; (**b**)—particle size; (**c**)—microstructure. It is anticipated that the absence of carbon in the composition of the selected HYF-103 powder (Table 1) will promote the improvement of service properties of printed products from austenitic materials due to the reduction of the formation of secondary phases of the carbide type [25]. The presence of boron in the powder composition will promote an increase in the equivalent concentration of nickel and will ensure the formation of a fine-grained austenitic structure. It is known that grain refinement is one of the most efficient methods to improve the material strength properties without increasing their brittleness. The effectiveness of boron influence, as an austenitizer, is quite high; for instance, boron is approximately a 10-fold stronger austenitizer than nickel [25]. Thus, the application of HYF-103 powder of a Fe-Cr-Ni-B-Si system for 3D printing via the additive deposition method is promising in terms of producing sufficiently hard and wear-resistant metal products with a high corrosion resistance and good tribological properties. However, during the layer-by-layer deposition of this material, zones of deformation localization with an increased level of residual stresses can form, which may lead both to cracking in the deposited layer material and to the development of defects of the printed geometry as a whole. This makes it necessary to assess and minimize the residual stress-strain state of basic spatial primitives printed by the selected method using HYF-103 powder.