## 2 Experimental Procedure  
### Materials and Processing Methods  
The samples of the Cu-SiC composite material were made from commercial copper powders (nanopowder, 98%, [PERSON] m\({}^{2}\)/g, OCHV, Moscow, Russia) and silicon carbide (abrasive micropowder F1200, 96%, LitFromAbrasive, Moscow, Russia) by spark plasma sintering. The powders were mixed in a ratio of 5, 10, 15, 20 wt.% SiC in isopropyl alcohol using an ultrasonic bath in order to achieve a uniform distribution of the components. Further, the resulting dispersed mixtures were placed in Petri dishes and dried for 120 h under laboratory conditions (at a temperature of 22-24 \({}^{\circ}\)C, relative humidity of 45-55%, atmospheric pressure). The portions of prepared mixtures weighing 4 g were used to fabricate bulk composite samples according to a well-tested procedure [40] by spark plasma sintering on an SPS 10-4 unit (GT Advances Technologies, Hudson, NH, USA). Simultaneous pressing and sintering were conducted in vacuum in graphite molds using graphite punches with a diameter of 12.7 mm at a pressure of 60 MPa. The initial powder sample was heated to a temperature of \(T_{\text{SPS}}\) = 700-850 \({}^{\circ}\)C at a rate of 100 \({}^{\circ}\)C/min with a unipolar current up to 5 kA. After holding at \(T_{\text{SPS}}\) for 10 min, the current supply was stopped and the samples were cooled to a temperature of 25 \({}^{\circ}\)C under a pressure of 60 MPa. The duration of the manufacturing process of a bulk ceramic sample did not exceed 30 min. The component composition, sintering conditions and characteristics of the fabricated bulk Cu-SiC samples are presented in Table 1.  
The reference sample No. 1 (copper) was sintered at a temperature of 850 \({}^{\circ}\)C. This was chosen based on specially conducted experiments, which showed that at a temperature below 850 \({}^{\circ}\)C, the density of the sintered sample significantly decreases. However, at temperatures above 850 \({}^{\circ}\)C, uncontrolled melting processes are realized. Using a Forcipol 1 V grinding and polishing machine (Metkon, Bursa, Turkey), the surface of the fabricated samples was mechanically processed by abrasive paper containing silicon carbide particles in order of decreasing grain size 320, 600, 800 and 1200 mesh. The modification procedure by laser radiation was conducted on preliminary polished Cu-SiC surfaces under laboratory conditions (ambient air, atmospheric pressure, temperature 20-22 \({}^{\circ}\)C, relative humidity 45-55%), using an ytterbium pulsed fiber laser (IPG Photonics, Moscow, Russia) as part of the TurboMarker-V50A4 RA system (Laser Center, Saint-Petersburg, Russia) with a wavelength of 1064 nm. An anisotropic texture with a multimodal developed roughness was designed according to a well-tested graphic-analytical technique [41] based on known geometrical shape and dimensions of the texture element (ablation crater). The selected type of texture makes it possible to change the wettability properties to extreme states (superhydrobilicity/superhydrob  
\begin{table}
\begin{tabular}{c c c c c} \hline \multirow{2}{*}{**Sample No. **} & \multicolumn{3}{c}{**Precursor**} & \multirow{2}{*}{**T\({}_{\text{SPS}}\), \({}^{\circ}\)C**} & \multirow{2}{*}{**Hardness, HV**} \\ \cline{2-2} \cline{4-5}  & **Cu, wt.\%** & & & \\ \hline
1 & 100 & 0 & 850 & 90 \(\pm\) 2 \\
2 & 90 & 10 & 800 & 124 \(\pm\) 3 \\
3 & 90 & 10 & 750 & 110 \(\pm\) 3 \\
4 & 90 & 10 & 700 & 107 \(\pm\) 3 \\
5 & 90 & 10 & 850 & 140 \(\pm\) 3 \\
6 & 95 & 5 & 850 & 138 \(\pm\) 3 \\
7 & 85 & 15 & 850 & 137 \(\pm\) 3 \\
8 & 80 & 20 & 850 & 141 \(\pm\)it possible to intensify the chemical reaction [42], heat and mass transfer [7] and phase transformations [43]. Special experiments were conducted to determine the geometric shape and dimensions of texture elements formed under the action of a single laser pulse on polished Cu-SiC surfaces.