Wetting Behavior and Functionality Restoration of Cold-Sprayed Aluminum-Quasicrystalline Composite Coatings

Coating design is an efficient strategy to engineer wettability of surfaces and adjustment of the functionality to the necessities in industrial sectors. The current study reveals the feasibility of functional aluminum/quasicrystalline (Al-QC) composite coatings fabrication by cold spray technology. A commercially available Al-based quasicrystalline powder (Al-Cr-Fe-Cu) was combined with aluminum alloy (Al6061) feedstock materials to make coatings with various compositions. A set of cold spray process parameters was employed to deposit composite coatings with different QC-Al ratios and Al6061 coatings as counterparts. The wettability of the coating surfaces was measured by static water droplet contact angles using a droplet shape analyzer and investigation of the dynamic of water droplet impact by high-speed imaging. Through microstructural studies, the Al-QC composites revealed dense structure, well-integrated and adherent deposits, providing structural reliability and enhanced hydrophobic behavior. In the last step of this work, composite coatings were deposited over eroded cold-sprayed Al6061 and a selected composite to demonstrate the feasibility of repairing the damaged part and function restoring. The results and approach used in this work provide understanding of cold-sprayed Al-QC composite coatings manufacturing and their wetting behavior state for cross-field applications.


Introduction
In many industrial sections, operational challenges exist when a component is in contact with water in the working condition. Corrosion, fouling, current leakage and heat transfer efficiency reduction, to name a few, are examples of such complications that can be avoided or reduced by employing hydrophobic coatings. By virtue of the low wetting feature, hydrophobic coatings can reduce water droplet contact and adhesion, interrupting unwanted interactions with water. Acknowledging immense potential applications, there has been an increasing interest in developing durable hydrophobic coatings in both academic and industrial fields ( Ref 1,2).
Wetting behavior can be determined by measuring water droplet contact angle (CA), defined as the angle between the water-air interface tangent and the water-solid interface (Ref 3). Surfaces with water droplet CAs of 90°\ H \ 150°a re considered hydrophobic, whereas higher and lower CAs might be classified in the categories of superhydrophobic and hydrophilic, respectively (Ref 4). Developing testing equipment enabled scientists to enrich their understanding of wetting by obtaining supplementary data from non-static testing methods such as impacted droplet dynamics (Ref [5][6][7]. A droplet hitting the surface might show different modes of splashing, spreading or rebounding, depending on the properties of liquid, impact condition (e.g., Weber number, hitting angle) and surface properties ( Ref 5). In case of waterrepellent surfaces, the impacted water droplets tend to bounce off from the surface and reduce their contact with the surface ( Ref 5,8). This scientific knowledge has led to the technical ability to design surfaces with regulated wettability for cross-field applications such as drag reduction, anti-icing, self-cleaning, corrosion protection, heat transfer enhancement and electricity generation, to name a few ( Ref 1,[9][10][11][12][13][14]. In general, surface chemistry modification and altering the surface roughness are effective strategies to fabricate waterrepellant surfaces ( Ref 1,[15][16][17][18]. However, the robustness of most effective candidates generally made through thin layer modification of surfaces, nanotextured surfaces, polymeric functionalization or fragile oxide layers is insufficient to fulfill the application-specific requirements, such as sufficient mechanical properties (Ref [19][20][21]. The types of structure that come out of nanoscale texturing and thin layer modifications are highly delicate and can be compromised during operation by environmental factors. In addition, mass production can be challenged by the facilities and processscale constraints and cost-related issues ( Ref 1,2). On the other hand, metals and metal alloys like Fe-and Al-based alloys as conventional materials in most structures and industrial sectors merely show hydrophilic behavior (Ref [22][23][24]. Therefore, facile generation of industry-scale and robust coatings with hydrophobic behavior is a pressing task. Thermal spray technologies with extensive possibilities can deposit versatile coating materials from soft polymeric materials to hard, brittle ceramics that meet the demands of the industry ( Ref 18,25). The efforts to fabricate non-wetting surfaces using thermal spray technologies consist of two main strategies: surface texturing and chemical modification of the surfaces ( Ref 12,[26][27][28][29][30][31][32]. To name some examples, two-step modification of the surface by flame spraying of nano-Al 2 O 3 (Ref 26) or suspension plasma spraying of TiO 2 (Ref 27) gave rise to water droplet CAs via producing a hierarchical roughness. Chemical modification of surface is followed in majority of wetting-engineered thermally sprayed coating. Controlled heat treatment of thermally sprayed coatings ( Ref 28), oil impregnation inside the structure (Ref 29), modification of thermal spray precursor with hydrophobic graphene-based structures (Ref 30) and deposition of low surface energy rare earth oxides (Ref 33,34) have shown increased hydrophobicity. The chemical treatment as a decisive step often is employed as posttreatment to avoid technical difficulties or unwanted heatsensitive components degradation by high heat input in the thermal spray processes ( Ref 32). Here, the potential of cold spraying with a significantly lower process temperature can be a game changer; it is possible to preserve the valuable phases in initial feedstock, heat-sensitive components and desired properties ( Ref 35). Cold spray can also address the in-service operational challenges; in a majority of applications, a coating made of a single material may not meet the requirement of service expectations, while functionality can be adjusted through designing a composite structure (Ref [36][37][38]. Moreover, cold spraying offers repairing possibility of the damaged part as another potential benefit; cold spraying is a green technology that uses inert gas, electric heating source with limited heat generation, capable of depositing coatings with desired mechanical properties without postprocessing ( Ref 35,[39][40][41]. Despite its many benefits, cold spraying is not as much explored as thermal spraying for fabricating non-wetting surfaces. ( Ref 18,25,42,43). These advantages can be used for successful fabrication Al-based alloys (Ref 44), as widely used engineering alloys used in industry with naturally hydrophilic behavior ( Ref 45).
In the current research, the aim was to incorporate micron-sized quasicrystalline (QC) powders into metallic coatings to alter their wetting performance toward hydrophobicity. Quasicrystalline materials with unique lattice structures have shown interesting physical and chemical properties different from well-known crystalline networks ( Ref 46). Studies on the properties of quasicrystalline materials have revealed sophisticated functional properties such as low surface energy, low friction coefficient, low conductivity, considerable hardness and electrochemical resistance (Ref [47][48][49][50]. Evidently, this category can be considered as candidate material for the fabrication of hydrophobic surfaces. Although thermal spray processes like high-velocity oxygen fuel (HVOF) and plasma spraying have been successfully employed in the deposition of hard and brittle quasicrystalline powders, the phase change during the high-temperature deposition is a constant challenge ( Ref 51,52). Furthermore, using QCs as reinforcing components in composite structures is a preferred strategy for avoiding mechanical problems caused by the inherent brittleness of these particles. A majority of the works reviewed in (Ref 53) have used powder metallurgy followed by sintering of compressed geometry or cooling rate-controlled melt solidification through conventional metal processing technologies for composite structure fabrication. Regarding the demonstrated capability and flexibility of cold spraying in composite production, our literature review revealed a possible knowledge gap due to the small number of studies, most of which largely focused on tribological and mechanical characteristics assessment ( Ref 52,[54][55][56]. Exploring the wetting characteristics of cold-sprayed QC-containing coating established the basis of this study, reflecting the practical interest in producing functioning surfaces. Coatings were produced by using pre-mixed Al-based QC powders and Al6061 (metallic powders) with a high-pressure cold spray system. Surface features, including topography, surface roughness and surface wettability of the coatings, were studied to evaluate surface properties of these Al-QC composites compared to metallic cold-sprayed Al6061 coatings. The potential linkages between the cold spray procedure and the produced microstructural characteristics are then thoroughly addressed. Ultimately, regarding the sustainability and potential of cold spraying in repair of these surfaces, erosion artifact on cold-sprayed coatings, and subsequent coating refurbish was carried out to provide a general picture of the restoration capabilities of the developed coating.

Experimental Procedure
Feedstock materials and coating process Three different powder compositions were selected with the following specifications: gas atomized aluminum alloy (Al6061, 10-40 lm as particle size distribution of d10-d90) supplied by TLS Technik GmbH & Co. (Bitterfeld, Germany) and two different size range of quasicrystalline Al-based powders (Cristome A1 with a nominal composition of Al53.9-Cr15.5-Fe13.8-Cu17.5 wt%, 10-30 lm called fine QC and 20-70 lm named as coarse QC, hereafter) supplied by Saint-Gobain Coating Solutions (Avignon, France). A high-pressure cold spray system, PCS-100 (Plasma Giken Co., Ltd., Saitama, Japan), mounted on an ABB robot arm (ABB Ltd., Helsinki, Finland), with nitrogen as the propeller gas was employed to accelerate the particles toward an Al-alloy plate vertically fixed as the substrate. For the composite coatings, the desired portion of each feedstock material was taken and mixed in a container and physically blended before transferring to the powder feeder (Plasma Giken Co, Ltd., Saitama, Japan. Table 1 contains the cold spray process parameters and sample coding for the investigated samples that were selected based on the preliminary testing with different compositions and process parameters. The codes in the table being used frequently in the text are generated based on the following argument: AlX-yQC where X is the volume percentage of Al6061 powders in the initial blend and y represents the size of QC powders that can be coarse (c) or fine (f). The substrates were degreased with ethanol and grit blasted using alumina grits (Mesh #40) prior to spraying the samples. An electrical heating plate was positioned behind the substrate allowing the surface temperature of the substrate to be stabilized (* 100°C) before beginning the spray procedure. This heating method was chosen based on previous coating optimization experiments that demonstrated the effects of in situ heat treatment on the microstructure and coating performance. A laser backlight-illuminated monitoring system, HiWatch HR2 (Oseir Oy., Tampere, Finland), was used to gain a better understanding of particle mobility in the gas stream. Feedstock materials were sprayed with the parameters used in coating fabrication without substrate while the stand-off distance (SoD) was set as the span of nozzle exit to focus plane of the laser system. The process started with realtime monitoring until the following criteria were fulfilled;

Characterization
A scanning electron microscope (SEM) (JEOL-IT500, Tokyo, Japan), operating at a 15 kV accelerating voltage, was utilized to observe the microstructure of selected test pieces. Secondary electron (SE) and backscattered electron (BSE, stereographic (BSE-S) mode) detectors were used to characterize the microstructure. The stereographic mode can concurrently accentuate compositional contrast and topographical characteristics, which are highly informative for composite surfaces. A parallel sample of each coating made in the same spray round was cut through the cross section using a precision cutter. Cross-sectional SEM samples were prepared by traditional metallographic methods including grinding and polishing of mounted specimen. ImageJ software package was utilized to measure the thickness and compare porosity level via at least five individual measurements. Surface roughness information was retrieved from an optical 3D profilometer, Alicona InfiniteFocus G5 (Alicona Imaging GmbH, Graz, Austria), with a focus variation working mechanism. The measured datasets from the desired area were scanned using Imagfield measurement by stitching 10 9 10 single measurements (100 neighboring zones with area = 2.81*2.81 mm 2 with overlapped boundaries). The final datasets subsequently were processed in the IF-MeasureSuite V 5.1 (Alicona Imaging GmbH, Graz, Austria), after form removing through the robust method. Primary datasets were used to visualize the surface texture, and the roughness component was filtered by a selection of proper cutoff wavelengths, following the approach employed in the literature (Ref 58) to extract relevant surface parameters.

Droplet shape analysis (DSA)
Sessile droplet static contact angle (CA) measurement was taken (room temperature 23.5°C ± 2°C, relative humidity of 50 ± 5%) using a droplet shape analyzer system (DSA100, Krüss, Hamburg, Germany). The procedure for CA measurement consisted of transferring a 5 ll droplet MilliQ ultra-high purity water (Millipore Corporation, Bedford, MA, USA) to the coating surface. Apparent CA was measured from the side view images taken from the shadows of at least 6 individual water droplets in the automatic procedure. Deformation of 10 ll droplets fallen from 10 cm height upon impact to the surfaces was visualized by installation of a 4000-fps high-speed camera (Memrecam fx K5, nac Image Technology, Salem, MA, USA) equipped with a 60-mm Nikon lens alongside a monochromatic light source at the side view of the stage. Before droplet shape analysis, the samples were cleaned with ethanol in an ultrasonic bath for 3 min to eliminate surface contamination and dried by cool air flow to accelerate the evaporation of ethanol. The samples were maintained in a desiccator cabinet for 1 day to assure removal of water content trapped in the coatings and later on, they were kept in the controlled condition room until the test day. Defect formation and repairing strategy A simplified plan was contrived to examine the viability of restoring the coating functionality by repairing the damaged part via cold spraying. A composite-coated specimen and a counterpart from aluminum alloy coating (Al50-fQC and Al6061, see Table 1) were fixed on a vertical plate and masked using a metal plate. A Dymet 403 (Obninsk Center for Powder Spraying, Obninsk, Russia) low-pressure cold spray system with air as the working gas and provided process parameters in Fig. 1(a) made an artificial defect on samples by eroding a 1.8 cm wide band. Inclined collision of coarse alumina (Al 2 O 3 ) particles with faceted morphology, sharp corners and angular edges according to features shown in Fig. 1(b) is likely to cause sufficient material removal (Ref 59). Therefore, the impact direction was set as 45°between the abrasive flow direction and coating surfaces. The damaged parts were recoated with two layers of Al50-cQC coating composition without heating the substrate. (The rest of process parameters are described in Table 1.) Wettability assessment and microstructural characterization were conducted on eroded band and repaired parts. In addition to optical surface roughness measurement of the desired area, a complete scan of each sample was measured in each phase and processed using the DifferenceMeasurement-module in IF-MeasureSuite software to evaluate the difference induced by each alteration. The datasets were finely overlapped using N point alignment in the intact area that was under mask during erosion and repair. Next, the difference between the datasets was extracted by a 3 lm threshold. The volume changes in the eroding band were then computed. Repaired sections were prepared using standard metallography procedure and observed using SEM and profilometer to probe the soundness of the deposits. Inspired by procedure used in (Ref 60, 61), interfacial Vickers indents with 0.5, 1, 3 and 10 kgf load were landed on the damaged/repaired interface using hardness testers (MMT-X7, Matsuzawa Ltd., Akita, Japan & Duramin-A300, Struers, Copenhagen, Denmark) for qualitative evaluation of interfacial adhesion.

Results
Feedstock Characteristics Figure 2 represents the morphology of feedstock powders. Quasicrystalline (QC) powders were generally spherical with slight deviation in geometry in two size ranges of coarse ( Fig. 2a) and fine (Fig. 2b). The QC powders surfaces possessed analogous surface textures and features.
The sporadic presence of satellites, small particles attached to main powders, can be detected in both distributions. Gas atomized Al6061 powder particles were spherical (Fig. 2c), with smoother surface texture and more satellites attached to larger powders compared to QCs. Both QC and Al6061 feedstock powders have random irregular particles marked with arrows in Fig. 2 (a-c). Figure 3(a) displays the HiWatch HR2 set up used for measuring the velocity of in-flight particles and heat-contour map of the particle velocity versus the position of particles in respect to the nozzle centerline ( Fig. 3(b)-(d) for Al6061, coarse QC particles and Al10-cQC feedstock combination, respectively). A symmetrical distribution from the centerline of nozzle (X = 0) indicates that inflight particles velocity of particles located near the core of jet have greater velocity. The mean velocity of particles was found to be lower than measured in-flight velocity of similar feedstock materials sprayed with higher temperature ( Ref 44). It is noteworthy to emphasize that using a same set of cold spray process parameters for Al6061 and composite structure was meant to avoid process parameters influence on coating formation. Microstructural properties of coating surface Figure 4 shows the microstructural features of examined surfaces. Spherical particles are frequent at the surfaces with visible particle boundaries from the last impacted particles. Nevertheless, underneath scattered spherical particles on the surface, denser structures were also generated by particles flattening through high-velocity impact that caused more deformation. In general, a wavy and rough topography was found all over the surface of coldsprayed Al6061 coating. The QC-Al composite surface formed where QC particles with heavier mean atomic mass appeared as the bright phases. Low magnification views of composite coatings in Fig. 4 illustrate a random distribution of QC particles over the composite surfaces. The higher magnification of Al10-cQC and Al50-cQC topography in Fig. 4 shows the dominancy of random craters as large as the coarse QC powders that hammered the surface and rebounded with micron-size fragment pieces leftover. Intact and fractured QCs, fragments and rebounded zones concomitantly exist on the examined composite surface. Exceeding fragmentation velocity-the velocity at which transition from rebounding to fragmentation takes place-is recommended to have a high content of brittle phase during cold spraying, although it leads to rarely intact particles left at the surface (Ref 62). The co-deposition strategy using a mixture of powders can help to contain a fraction of QC particles pinned in the structure in its original morphology as well. Material flow at the edges of the craters can be seen regularly all over the surface.
Using finer QC particles in the initial powder feedstock mixture revealed a slightly different morphology on the composite surfaces. Smaller in size but higher in number, rebounded zones in Fig. 4 generated a finer dimple-like features over larger scale dome-like structure. The rough top surface made it difficult, if not impossible, to accurately measure and compare the relative content of each phase. In addition to the roughness that interferes with image processing, the minute, dispersed bits of QC powders clinging to the soft phase are difficult to account for in the image analysis.
Multiscale surface textures, consisting of large-scale waviness and micron-scale roughness, were generated through cold spray process. This is a typical surface  Therefore, it is reasonable to shift the focus toward surface parameters and comprehend their meaning. The areal surface roughness parameters for the studied coatings are presented in Fig. 5. Sa, described as the height amplitude of the selected area, is a commonly used surface parameter. Sa generally is an indication of surface roughness and correspond to definition of Ra in the line profile scan. Sp, Sv and their sum Sz are other height parameters representing the maximum peak height, the deepest valley depth and maximum height of the selected surface. S10z is an extended parameter that corrects outlier influence on the measured area by considering five tallest peaks and five deepest valleys in the calculation of the largest heights. Information regarding the distribution of height can be explained by skewness (Ssk) and kurtosis (Sku). In positively skewed (Ssk [ 0) surface high peaks dominate at the surface while negative Ssk implies that surface is mostly made of deep valleys. The kurtosis value defines the sharpness of irregularities where surfaces with Sku [ 3 and Sku \ 3 have sharper and blunter features, respectively, while Sku = 3 means equal distribution of blunt and sharp asperities and valleys. Sdr is defined as the developed interfacial ratio implying the surplus area generated by  Cold-sprayed Al6061 coating shows high Sa and S10z values. But for coldsprayed composite coating, these values declined with increasing content and size of QC particles used in the feedstock. As explained for the morphology of surfaces (Fig. 4) Possible factors in ranking the order of kurtosis value of the coating surfaces could be the jets at the crater edge of nonadhering particles, fractured particles sharp edges and sporadic fragments. In brief, Al6061 coating showed remarkably high surface roughness with a large difference between the peaks and valleys, which caused a significant increase of real surface area. Regarding surface roughness parameters, cold-sprayed composite coatings typically had smoother surfaces, smaller but pointier asperities, and less additional surface produced by roughness than the coldsprayed Al6061 coating had. The dominance of peaks at the surface of Al10-cQC produced by the severe hammering of structure is a notable distinction between surfaces. Surface roughness measurements showed a clear difference between Al10-cQC and Al50-cQC, indicating that an increase in QC content in the feedstock materials led to a decrease in roughness and creation of additional surfaces.

Microstructural Characteristics of Coating
Cross section of the cold-sprayed Al6061 sample (Fig. 6a) revealed a thick deposit (514 lm ± 78 lm) due to relatively high deposition efficiency of ductile aluminum particles ( Ref 35,44), but disconnected random pores (black spots in Fig. 6(a) and corresponding inset micrograph) were found across the cross section, especially closer to the surface where the hammering effect from subsequently impacted particles is marginal (Ref 36. The cross sections of composite coatings are presented in Fig. 6(b)-(d).
Interestingly, denser coatings with an almost uniform distribution of QC and Al6061 particles were produced. Achieving such an improvement in structure implies the positive effect of QC particles in the densification of the coating, sprayed with the same cold spray process parameters. The volume ratio of QC/Al in the initial feedstock (provided in Table 1) declined within the composite structures due to the rebounding of hard QC powders. Blending of feedstock materials for composite coating formation is a straightforward and feasible method, but the distribution of phases cannot be engineered during the process (Ref 38,66). Comparably, deposition efficiency was lower for the composite coating with higher QC content (t Al10-cQC = 310 lm ± 16 lm \ t Al50-cQC-= 668 lm ± 27 lm). It is noteworthy to mention that the deposition efficiency is estimated by comparing the thicknesses. The notable difference is that, when sprayed with the same cold spray process settings, Al50-cQC exhibits higher coating thickness and densification degree than Al6061 (Fig. 6a and c). Having reinforcing phases in the initial blend of feedstock positively influences the tamping effect and deposition efficiency at the same time (Ref 36). Nevertheless, loading extensive hard particles increases the tamping and densification at the expense of non-effective collision and can decrease deposit efficiency, as deposition is still governed by the ductile metallic phase. The latter was valid for Al10-cQC sample, even though the chosen ratio was intended to maximize QC particle coverage on the top surface. On the other hand, the composite coating containing fine QCs (Al25-fQC) did not show significant improvement in terms of densification and deposition efficiency of the coating compared to counterparts containing coarse QCs (see Fig. 6d). Image analysis estimated the share of QC phase in the cross section of Al25-fQC composite structure at 18.2 vol-%, whereas Al10-cQC and Al50-cQC have higher average values of 50.1% and 19.4%. Coarse QC particles had a higher contribution to the final structure by taking the QC volume fraction of the initial feedstocks into account. The highest QC fraction that was calculated for Al10-cQC was higher than in the earlier researches of cold-sprayed QC-containing composite coatings ( Ref 54,55). Increased porosity has been reported after increasing hard QC content up to 30% in the coating structure (Ref 54). Remarkably, the porosity level was lowest for the coating with the highest QC content; all coatings were denser than the Al6061 coating with 2.82 ± 0.74 vol% porosity, although QC particle size had a greater influence on void reduction (average pore vol% excluding the outliers near interfaces of cross sections: Al10-cQC \ 0.10 pore vol%, Al50-cQC = 0.24 ± 0.09 pore vol%, Al25-fQC = 0.95 ± 0.27 pore vol%). These findings support the argument that larger particles with more inertia have better tamping or hammering effect of the coatings upon impact (Ref 67). sprayed Al6061 coatings showed hydrophilic behavior; water droplets tended to continuously spread shortly after placing on the surface. Visually, wetting marks multiple times larger than original droplet diameter appeared after the disappearance of the water droplet on surface. A possible reason could be the microstructure of coating with connected network of pores and heterogeneities that helps spreading water through narrow pathways (Ref 68). Furthermore, the hydrophilic nature of untreated aluminum alloys has been already confirmed (Ref 23,69). It has been also found that keeping the bulk aluminum alloy in atmospheric conditions slightly increases the CA due to absorbance of airborne organic compound from the atmosphere. However, in all trials of water on cold-sprayed Al6061, surface showed the vanishing behavior with CA \ 10°a fter sample storage in the atmosphere more than 6 months. On the other hand, composite coatings showed drastic increase of CA and all values were higher than 90°which is an arbitrary, but commonly accepted, threshold for hydrophobicity. Al10-cQC had the highest CA exceeding 150°followed by Al50-cQC and Al25-fQC with CA * 141°and 120°, respectively. The standard deviation for multiple CA measurements (the error bars in Fig. 7) was low for each surface implying a homogenous wetting all over the surfaces. The CA values remained constant up to 30 min after droplet positioning. Despite high CA, droplet mobility was not observed for composite structures in rolloff or sliding CA conditions. The droplet remained pinned to surfaces even after tilting of the stage exceeding 30°. Similarly, despite an increased CA, limited droplet movement is reported in several research works (Ref 33, 42, 69).

Wetting Assessment
In the previous section, it was mentioned that surface roughness and chemistry (QC/Al at surface) are tightly interconnected to the feedstock combination used. To confirm the role of roughness/texture on hydrophobicity, Al6061 and Al10-cQC wetting behavior was compared after analogous mechanical polishing of their counterpart surfaces. In polished state, the Al6061 and composite coating showed hydrophilic state. Al10-cQC lost its hydrophobicity (CA = 64.8 ± 6°) after removing the roughness of surface, and Al6061 gained relatively stable CA up to 30°(see Fig. 7). Evidently, surface roughness effect is significant though the quantitative Interaction of surfaces with the impacted water droplets provides additional information regarding the wettability of tested surfaces. Deformation of water droplets upon impact on horizontally fixed coating surfaces has been visualized with high-speed optical imaging. (Videos captured from impacted droplet are provided in supplementary materials.) Selected frames in Fig. 8 contain information about the deformation state of the droplet at a recorded time, measured from first contact between the droplet and surface. From the contact point, droplets began to flatten radially over all surfaces, and the contact area for each case increased until the maximum spreading state was reached. Starting the recoiling phase, the difference between surfaces emerges through dissimilar recoalescence of spread droplets. On composite coating surfaces, the radial momentum changes direction to an upward direction and forces the droplet to detach from the surface. Tendency to rebounding was observed, although partial rebounding happened only on Al10-cQC, confirming higher repellency among the tested surfaces. The droplet was divided into two large segments and several smaller satellite droplets. The detached component rejoined the pinned portion, and oscillation proceeded without further bouncing. The impacted droplets on the other composite coatings failed to rebound and adhered to the surface. On the other hand, Al6061 coating surface prevented water droplet recoiling and preserved the spreading dimension near the maximum spreading diameter. During water spreading and recoiling, the kinetic energy of the droplet dissipates to compensate for the interfacial forces (droplet-surface interactions), which are higher for hydrophobic surfaces. Consequently, the kinetic energy is insufficient to reassemble the droplet and cause it to rebound off the surface (Ref 68). The droplet settled in the flattened form at the surface while the droplets stayed pinned on composite surfaces with hemispherical contour and prolonged oscillation till the end of recorded frames. Noteworthy to mention that the final droplet image in Fig. 8 for each trial was the end frame of the trigger. Visually, their final state possessed reduced CA with a larger area wetted underneath of droplets compared to their CAs in Fig. 7 where the droplet was gently placed on the surfaces. One possible reason according to experiments carried out on pillar textured surfaces (Ref 68) could be the influence by impact kinetic energy, which increased water droplet penetration into surface features in the impact zone, causing sticking and wetting of a broader area.

Repairing the Artificial Defect
The idea of repairing the damaged part was initiated via mimicking a significant surface damage through creating erosion artifacts. The surface of Al6061-and Al50-fQCcoated samples was characterized after a certain area of each piece was eroded by sharp alumina (Fig. 9). The texture presented in Fig. 9 results as a calculation of the difference between datasets before and after erosion. The intact parts of the tested specimen in greenish texture are set as zero level, and deviation from the initial state is highlighted by a depth color map; for example, deep grooves (depth higher than 100 lm) are pronounced in eroded bands of both coatings and are highlighted in blue spectrum color. Morphology of the sample has changed significantly by erosion marks appearing in SEM images; abrasive scars, including ductile scoring, material smearing (marked by arrows) and intruded abrasive alumina particles, were found. QC particles in the composite coating were not detached from the composite structure, and the abrasive path continued over QCs rather than detaching particles, as it is presented in Fig. 9(b) III. Visually, the number of intruded abrasives in the composite coating was found to be lower compared to Al6061 eroded band during the scan of the whole surface using SEM. The volume loss measured in the eroded region was another distinction worth noticing. The volume removed from the Al6061 coating was 41% higher than from the composite coating. It is worth recalling that the composite coating had the least QC particles inside the structure among the studied samples in this work. Due to currently limited information, a direct conclusion about enhanced abrasion resistance of composite coatings is not possible.
Water droplets had the same behavior on both eroded surfaces, although QC particles retained at the structure has an influence on chemical composition. Assuming the fact that erosion occurred at low temperature had a negligible influence on the chemical characteristics of the surface, the intruded alumina abrasives that intermittently emerged at the surface might be a tangible factor affecting the surface chemistry. In contrast, the surface parameters of the eroded regions are comparable independent of their as-sprayed surface parameters (see Fig. 5) and compositions (Al6061 eroded band: Sa = 12.5 lm, S10Z = 155.5 lm, Ssk = 0.0, Sku = 3.2 and Sdr = 47.3%; Al50-fQC eroded band: Sa = 10.4 lm, S10Z = 131.0 lm, Ssk = 0.02, Sku = 3.34 and Sdr = 43.3%). This discovery once again underscored the significance of surface features in conjunction with the presence of QC particles as determinants in shaping the droplet and its CA. Figure 10 illustrates the structure and shape of the water droplets on the surfaces repaired by cold spraying of Al50-cQC. The 3D texture profile provided in Fig. 10 I represents the difference of repaired and eroded samples. Successful and consistent coating build-up entirely covering the eroded strips can be confirmed using the color gradient and by setting purple color as zero level corresponding to the masked intact area. Visually, restored surfaces exhibit waviness resembled to that of sprayed coatings on gritblasted substrates, with no discernible effect from the eroded layer roughness/waviness. Furthermore, topographical characteristics on the surface of mended portions were almost identical. Deformed Al6061 powders, rebounded impact zones, non-deformed QC particles with their original texture, fractured and fragmented QC particles altogether can be found on the surface (Fig. 10II). These findings validate the similarity between the water droplet forms and intimate CAs observed on both surfaces. Both repaired coatings revealed the average water droplet CA comparable to Al50-cQC coatings applied as the  Cross section of the repaired parts in Fig. 10 III indicates that the cold spray process developed a proper bonding between the restored coating and eroded surface for both samples. Trapped abrasives appeared in gray color at the interface of eroded coating leftovers and new coatings. Generally, the bonding of repaired coating to the eroded surface was strong so that interface could only be tracked with the help of the entrapped abrasives. However, no significant effect was observed due to abrasive entrapment in terms of bonding of the repaired coating. Entrapped abrasives do not necessarily interfere with the operation of the thermal sprayed coatings, if not enhance the continuing-substrate adhesion. Generally, grit blasting prior to coating deposition enhances interlocking at the interface of coating with sublayer without meddling with coating properties and surface functionality (Ref 60, 70). At the interfaces, there are no evident signs of delamination or substantial interfacial voids, despite slightly larger pores appeared in the repaired coating compared to their Al50-cQC counterpart sprayed on aluminum plate. Possible explanations include differences in process parameter settings, such as the heating plate behind the specimen, and fewer layer applied in repairing trial (2 layers) compared to Al50-cQC (3 layers) that may result in extra deformation to the underneath structure.
The interfacial indents were used to assess the integrity of repaired interfaces. The indents with loads equal to 1 kgf and less did not propagate visually significant cracks along the interface. Indents landed on random interfacial spots implying a proper interfacial bonding across the studied coating cross section. When loaded by Vickers indents with varying loads, QC particles act brittle and tend to propagate cracks as large as the particle diameter. Nonetheless, the cracks did not extend beyond the indent-landed QC particle (see Fig. 11a with indentation load of 3 kgf). Figure 11b demonstrates a narrow crack follows the interface path once interfacial indent with 3 kgf load was applied. In this context, material flow and plastic deformation at the edges of indents without tearing the boundaries of adjacent bonded particles indicates a satisfactory level of integrity. Note that higher indentation load (10 kgf) failed to provide a reliable result as it led to enlarged indent marks that exceeded coating thickness. These observations indicate that the repaired parts are well-bonded to the eroded parts.

Cold-Sprayed Al-QC Composite Coatings-Microstructure and Wetting Behavior
Investigation of surface wetting is typically accompanied by exploring surface chemistry and roughness. There is a number of studies on surface roughness modification, provided the surface chemistry remains constant (Ref 27,58). Aside from the fact that even minor surface interaction with the environment might produce chemical changes, establishing a window of surface roughness parameters within which a specific wetting behavior can be seen is not a feasible approach. On the one hand, exceptional hydrophobicity of a suspension plasma-sprayed TiO 2 coating ( Ref 27) and, on the other hand, enhanced hydrophilicity of modified TiO 2 surfaces produced by HVOF have been correlated with surface dual roughness (Ref 31). In the majority of cases, the highly hydrophobic behavior of thermally sprayed coatings only has appeared after a further chemical modification of feedstock or coating with hydrophobic agents (Ref 26-28, 31, 42). Thus, the idea of having a hydrophobic surface that requires minimal post-processing was the incentive behind testing different sets of coatings in this work, aiming to engineer a facile production of hydrophobic surfaces by cold spraying.
The cold-sprayed Al6061 coatings produced with the same parameter used for cold-sprayed Al-QC composite coatings demonstrated the highest level of porosity among the tested samples. Al6061 coating has been deposited efficiently in a range of cold spray parameters that provides a velocity higher than the critical velocity needed for deposition (Ref 44,67,71), typically with gas pressure higher than N 2 pressure used in this work. Plastic deformation of Al6061 particles took place easier than QC particles; consequently, it acted a binder phase embracing the hard QC particles that are prone to cracking and fragmentation. Similar deformation mechanisms are wellknown in cold spraying of metal matrix composites in which the reinforcing component is comprised of hard particles, particularly ceramics (Ref 37  37,74). In Al-QC composite coatings, entrapment of the QC fragments in the structure of the coatings between the passes of deposition, as it was found in Fig. 6 (small bright phases randomly distributed in the coating), might impose effect on the coating mechanical properties ( Ref 72,73). Better understanding of this effect needs further in-depth study on microstructural dependency of mechanical properties. A steady decline in the CA over time might occur due to the water penetration inside pores and grooves between semi-deformed particles, as has been observed in HVOF cermet coatings with a porous structure (Ref 28). The surface free energy of the material also influences the tendency of water droplets to spread over high energy surfaces or to keep its binding with water molecules and retain spherical droplets in contact with low energy surfaces ( Ref 15,30,33). Compared to earlier studies (Ref 23,24), the gradual disappearance of water droplets over cold-sprayed Al6061 coatings in the current study was not surprising.
The concept of wetting has been under investigation for many years, yet there is no general agreement about the underlying mechanisms ( Ref 2,16,17); Very fine-scale complexity and heterogeneity of real surfaces, nature of liquids and testing condition were found to be sources of deviations from well-known wetting models. Nevertheless, the classic models are still being used to justify the wetting states. Two well-known classical models were proposed by Wenzel (Ref 75) and , which include the roughness of the surface as a critical factor in their explanation. Wenzel has supposed that the infiltration of water into surface roughness and filling the grooves wet actual area larger than the projected area and causes higher surface energy reduction. Cassie and Baxter have suggested that water cannot fill the whole area under water droplets resting on rough surfaces due to trapped air inside the gaps of rough surfaces. Thus, the droplets stand suspended on top of rough surfaces with air pockets trapped underneath, showing an increased apparent CA and mobility. These models are still being widely used in describing the hydrophobicity evaluations ( Ref 15,21,27), although there are opposing experimental proofs debating the basics (Ref 77). Here, the likely scenario behind the remarkable CA increase can be described as the effect of two factors; crater-like attributes and an overall surface energy reduction generated in the cold spray process: Here, feedstock combination caused diverse roughness features and chemical composition at the surface that led to different wetting conditions. Wettability of cold-sprayed Al-QC composite coatings is obvious examples that confirm that the effect of surface roughness and chemistry is synergistic, and it is rather difficult to discuss their individual effects separately.

Feasibility of Repair and Restoring Properties
Coating mechanical properties, facile methods for mass production, applicability for different purposes and longterm stability are some of the challenges in the industry ( Ref 1,19,20); given that high endurance from coldsprayed Al-QC could be retrieved, it is also interesting to tackle the other challenges such as extending the functionality. In accordance with earlier studies in cold spray composite structures ( Ref 36,66,74), QC particles improved the bonding strength and coating density and with specific combinations, it improved the deposition efficiency. However, preserving the properties and refurbishing the components coatings feasibly are also pushing forward to explore them into the structural details.
A number of research works focused on the repairing approach using cold spraying techniques primarily seeking to achieve acceptable mechanical qualities in the restored component ( Ref 39,79). Although it is vital to match the mechanical properties of the main part, repairing should strive to recover other functionalities as well. Regeneration of the structure needs a certain procedure that might be overreaching for delicately patterned or nano-structured coatings (Ref 80). The current results showed that after erosion, hydrophobicity declined due to substantial changes in surface roughness, although in terms of chemistry, QC particles remained at the surface (see Fig. 9b). In turn, repairing the coating was a feasible and straightforward process, which was fruitful in terms of repaired part integrity, substrate type and state flexibility (grit-blasted plate, eroded Al6061 coating, eroded Al-QC composite coating) and hydrophobicity restoration through fast regeneration of the coating layer covering the damaged area without further pre/post-processing. Although the amount of pores appearing in the repaired parts was slightly higher than in the Al-50cQC cold-sprayed coating, by selecting higher process parameters close to what has been used in the earlier works this deviation might be eliminated ( Ref 35,67). Less volume loss is a clue of enhanced erosion resistance of the subjected composite coating, considering some debates on the coldsprayed composite structure cases (Ref 37, 81) suffering from the reinforcing phase fracture, detachment due to poor interfacial bonding, and debonding of layers under load. Hence, studying tribological qualities is a compelling topic to be continued in the future.
Cold-sprayed Al-QC composite coatings are intriguing because they exhibit enhanced, new or mixed features in comparison with the properties of their constituents. Other combinations may also exhibit improved hydrophobicity; a transition toward hydrophobic behavior was seen for a relatively hydrophilic stainless steel surface-one of the most frequently used materials in structures ( Ref 82). It is established that cold-sprayed composite surfaces with QC particles and altered wetting behavior can be expanded to various alloys as well ( Ref 82). Nonetheless, a more systematic study is still needed to have a better understanding of coating integrity, structural details and mechanical properties of the developed Al-QC composite structures.

Conclusion
High-pressure cold spraying was used to fabricate composite coatings by feeding different blends of Al-based quasicrystalline and Al6061 feedstock powder materials. The presence of QC particles, in different sizes and content in the cold-sprayed metallic composite coatings surfaces, was found to be a practical approach to change the surface wettability through a one-step process. The cold-sprayed Al6061-coating demonstrated highly hydrophilic behavior in the as-sprayed condition. In contrast, hydrophobic behavior was achieved through incorporation of QC particles in the structure (119°\ CA \ 153°and tendency to rebound the impacted droplet) owed to the dispersion of low surface energy QC phase on the surface and modification of surface roughness and texture in the cold spray process. The composite coating with a high load of larger QC particles (Al 10 vol-% ? QC 20-73 lm) was superior in terms of densification and enhanced hydrophobicity by providing a dimple-like structure with sharp asperities and less open porosities in the structure. Furthermore, cold spraying enabled repairing the artificial erosion damage by successful deposition of well-bonded composite coating without prior surface preparation. The erosion condition using abrasive alumina was chosen as severe enough to cause significant damage and alteration of surface features. The cold-sprayed composite coating structure showed less volume loss due to erosion compared to the Al6061 counterpart. Nevertheless, repairing by cold spray was successful in refurbishing the coating and regaining hydrophobicity.
Acknowledgments Authors would like to thank Mr. Jarkko Lehti and Mr. Anssi Metsähonkala of Tampere University for spraying the coating samples, and Dr. Jari Rämö and IMPACT group of Tampere University for their sincere help and provided resource in high-speed imaging. Tampere University, the Faculty of Engineering and Natural Sciences is acknowledged by R.J. for the funding. SEM work made use of Tampere Microscopy Center facilities at Tampere University, Finland. This research was partly funded by Academy of Finland, project ''Thermally Sprayed slippery liquid infused porous surfacetowards durable anti-icing coatings'' (TS-SLIPS).
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