Advanced Functional Metal-Ceramic and Ceramic Coatings Deposited by Low-Pressure Cold Spraying: A Review

Based on the recent analysis of various databases, cold spray (CS), the newest method among thermal spraying technologies, has received the unabated attention of hundreds of researchers continuously since its invention in the 1980s. The significance of CS lies in the low process temperature, which usually ensures compressive residual stresses and allows for the formation of coatings on a thermally sensitive substrate. This paper concerns the low-pressure cold spray (LPCS) variant employed for forming metal matrix composites (MMCs) with high ceramic contents and all-ceramic coatings. At the very beginning, the influence of LPCS process parameters on deposition efficiency (DE) is analysed. In the next part, the most useful feedstock powder preparation techniques for LCPS are presented. Due to the combination of bottom-up powder production methods (e.g., sol-gel (SG)) with LCPS, the metal matrix that works as a binder for ceramic particles in MMC coatings can be removed, resulting in all-ceramic coatings. Furthermore, with optimization of spraying parameters, it is possible to predict and control phase transformation in the feedstock material. Further in the paper, differences in the bonding mechanism of metal–ceramic mixtures and ceramic particles are presented. The properties and applications of various MMC and ceramic coatings are also discussed. Finally, the exemplary direction of CS development is suggested.


Introduction
Cold gas dynamic spraying, also known as kinetic spraying or simply cold spraying (CS), was originally developed in the mid-1980s as a coating deposition process by A. Papyrin and his team at the Institute of Theoretical and Applied Mechanics of the Russian Academy of Sciences in Novosibirsk [1]. Russian researchers reported several patents, including [2][3][4], and then published the first manuscript on CS in 1990 [5]. This invention was outstanding in the field of thermal spray technologies as the process enabled the deposition of solid-state metal particles. While improving the CS process, Papyrin's team successfully deposited a wide range of pure metals, metal alloys, and metal-ceramic composites on a variety of substrate materials and demonstrated the feasibility of cold spraying for various applications. To safeguard this innovative technology in other continents, a U.S. patent on CS was issued in 1994 [6], and a European one in 1995 [7]. Until now researchers all over the world have been developing the CS process and widening its applications.
CS compared to other thermal spraying techniques is characterized as a low-temperature process [8,9]. Thermal energy necessary for powder deposition is replaced in CS by kinetic energy. The working gas gains supersonic velocity in the de Laval nozzle and, due to drag force, accelerates the powder particles. The velocity can be controlled by the pressure and temperature of the gas. In addition, the process temperature increases the plasticity of the metal particles, enabling mechanical bonding. Nevertheless, the melting point of the applied powder material is not exceeded and thus the particles are sprayed in the solid state. Low thermal energy generates many benefits, such as: (i) high coating purity with photocatalytic efficiency [54]. These improvements can be achieved in CS coatings by tailoring the composition and microstructure of the composite or ceramic powder. However, the control of nanostructures in the coating via powder preparation and processing parameters remains a challenging issue.
After three decades of worldwide research on the CS process, more and more unique functional materials (such as composite or ceramic nanomaterials) are being found, increasing the possible range of applications. LPCS seems to be especially promising as an economic, mobile, safe and easy-to-operate system. Within the presented paper, modern applications of LPCS divided into metal-ceramic composite and al-ceramic coatings are discussed.

LPCS Deposition Efficiency
It is commonly known that HPCS has superior deposition efficiency (DE) over LPCS due to significantly higher process parameters (e.g., pressure and temperature). Taking aluminium powder as an example, the DE equals 95% for HPCS [25] and 7% for LPCS [48,55]. As one may guess, additive manufacturing using LPCS has very limited capabilities. LPCS, however, has several advantages over HPCS from an economical point of view, concerning gas consumption, installation and maintenance cost [1,25,27]. Therefore, optimization of LPCS process parameters using commercially available or self-synthesized powder materials provides access to the advanced functionalization of substrate surfaces for various applications in many industrial fields.
A basic method to improve the DE in LPCS is mixing soft metal powder with hard phase, e.g., ceramic powder, which provides a tamping effect and increases plastic deformation [48]. As a result, more metal powder will be embedded with additional ceramics. Nevertheless, the size of the ceramic particles in the mixture significantly affects the DE of the powder. Sova et al. [56] found that only fine ceramic particles in powder significantly increase the DE of the metal component due to the roughening, cleaning, and mechanoactivating of the surface or previously sprayed metal particles. What is more, coarse particles decrease the DE due to lower velocity and enhanced erosion of the surface [57]. On the other hand, the particle mass loading influences significantly their acceleration by working gas. By using numerical calculations and experimental verification, Meyer et al. [58] revealed that increasing the feed rate up to 120 g/min caused a decrease of particle velocity of 14%. It is worth emphasising that in LPCS the most popular feedstock are powders mixtures with a particle size of 5-50 µm [59,60]. The DE of particles out of the range is limited due to lower velocity. It results from high mass or deceleration in the bow shock region for larger and smaller particles, respectively. Another factor influencing DE is metal powder shape. Dendritic or irregular metal particles deform easier than spherical [61]. Application of spherical and dendritic copper powder in LPCS resulted in DE = 6.9% and 28.6%, respectively [62]. Further admixture of hard phase to dendritic powder increases DE to 35.8%. Melendez and McDonald [63] sprayed tungsten carbide (WC) + 4 wt.% Ni powder mixture and obtained DE of WC equal to 68%. It is generally stated that DE of LPCS remains low and does not exceed 40% with common process parameters [64]. However, there are other more demanding methods to increase DE based on application, including laser-assisted cold spray process [65], powder feedstock oxide reduction before spraying [66,67], long preheating of the powder feedstock [21], additional heating of the substrate during spraying [61,68], as well as utilizing another working gas instead of air [61,68,69].
It is advisable to start the DE optimization with proper LPCS process parameters selection. The parameters can be categorized into four main types [70]: gas parameters, nozzle geometrical parameters, particle parameters, and substrate parameters ( Figure 1). Those parameters influence the critical velocity of particles. According to the literature, the deposition efficiency is determined by the ratio of particle exit velocity to the critical velocity [26,69]. As a result, using a proper mathematical model, the DE can be calculated [5]: Raoelison et al. [69] applied 1-D computing tests of the gas flow through the de Laval nozzle and by the interaction with the particles identified potential solutions to increase the DE. Using air as a propellant gas set at 10 bar and 630 °C and particles with a diameter higher than 10 µm, resulted in the maximum DE of 20% (see Figure 2). What is more, particles with a diameter above 15 µm will rebound. To increase the DE up to 90% or more, LPCS parameters, such as particles size, working gas, nozzle length, and expansion ratio, should be adjusted (Table 1). Nevertheless, according to Raoelison et al. [69], the highest influence has the working gas. Helium, compared to nitrogen and air, remains the most efficient gas due to its high specific gas constant. It is worth emphasizing that the standoff distance (SoD) of the nozzle to the substrate is crucial for particles velocity and should be between 5 and 15 mm. When the SoD increases, the gas velocity decreases due to viscous effects at the spraying jet periphery. However, the gas velocity remains supersonic for the longest time at the centre of the jet, since here the gas velocity is highest [70] ( Figure 3). Table 1. Influence of LPCS parameters on the DE (inspired by Raoelison et al. [69]).

LPCS Process Parameter Positive Impact (Advantages) Negative Impact (Disadvantages)
Decrease of the particles size below 3 µm High DE, up to 70% Tend to stick on the nozzle wall and cause clogging Change the nozzle expansion ratio (r-exit/r-throat): 1.2-2.0 Higher particles velocities -Increase the length of the diverging part of the nozzle from 130 to 400 mm For the particle diameter of 10 µm, DE increase from 20% to 50% Long nozzle may cause: (i) vibration of the nozzle exit part, (ii) bending of the overheated nozzle Raoelison et al. [69] applied 1-D computing tests of the gas flow through the de Laval nozzle and by the interaction with the particles identified potential solutions to increase the DE. Using air as a propellant gas set at 10 bar and 630 • C and particles with a diameter higher than 10 µm, resulted in the maximum DE of 20% (see Figure 2). What is more, particles with a diameter above 15 µm will rebound. To increase the DE up to 90% or more, LPCS parameters, such as particles size, working gas, nozzle length, and expansion ratio, should be adjusted (Table 1). Nevertheless, according to Raoelison et al. [69], the highest influence has the working gas. Helium, compared to nitrogen and air, remains the most efficient gas due to its high specific gas constant. It is worth emphasizing that the standoff distance (SoD) of the nozzle to the substrate is crucial for particles velocity and should be between 5 and 15 mm. When the SoD increases, the gas velocity decreases due to viscous effects at the spraying jet periphery. However, the gas velocity remains supersonic for the longest time at the centre of the jet, since here the gas velocity is highest [70] (Figure 3). Table 1. Influence of LPCS parameters on the DE (inspired by Raoelison et al. [69]).

LPCS Process Parameter Positive Impact (Advantages) Negative Impact (Disadvantages)
Decrease of the particles size below 3 µm High DE, up to 70% Tend to stick on the nozzle wall and cause clogging Change the nozzle expansion ratio (r-exit/r-throat): 1.2-2.0 Higher particles velocities -Increase the length of the diverging part of the nozzle from 130 to 400 mm For the particle diameter of 10 µm, DE increase from 20% to 50% Long nozzle may cause: (i) vibration of the nozzle exit part, (ii) bending of the overheated nozzle Apply helium as working gas Helium alone enables a great increase of DE due to its high specific gas constant Extremally higher costs of the process Apply helium as working gas Helium alone enables a great increase of DE due to its high specific gas constant Extremally higher costs of the process  It is well known that the higher velocity of impacting metal particles in CS the higher deformation and DE [70]. However, the velocity should not exceed erosion velocity, in which substrate degradation occurs ( Figure 4). The range between critical velocity and erosion velocity restricts a deposition window. It is visible in Figure 4 that the range is Apply helium as working gas Helium alone enables a great increase of DE due to its high specific gas constant Extremally higher costs of the process  It is well known that the higher velocity of impacting metal particles in CS the higher deformation and DE [70]. However, the velocity should not exceed erosion velocity, in which substrate degradation occurs ( Figure 4). The range between critical velocity and erosion velocity restricts a deposition window. It is visible in Figure 4 that the range is It is well known that the higher velocity of impacting metal particles in CS the higher deformation and DE [70]. However, the velocity should not exceed erosion velocity, in which substrate degradation occurs ( Figure 4). The range between critical velocity and erosion velocity restricts a deposition window. It is visible in Figure 4 that the range is broad for ductile metals. What is more, Schmidt et al. [71] concluded that brittle materials (e.g., ceramics) would cause erosion for any velocity as long as their temperature is below the melting point. Kliemann et al. [72] tested HPCS to spray TiO 2 coating on various

Metal Matrix Composite Coatings
Particle reinforced metal matrix composite (PRMMC) coatings consist of a ductile matrix (pure metal or metal alloy) and hard reinforcement phase (different metal, ceramics, intermetallic phase, organic or inorganic material), and as a result, combine properties of both materials, e.g., resistance for high-temperature mechanical loading, maintaining increased durability [77,78]. Due to high strength, hardness, chemical inertness, high melting point, and many functional applications, ceramic powder is the most commonly selected material for reinforcement in PRMMC coatings [77,[79][80][81][82]. The uniformly distributed, coherent, and continuous hard phase in the metallic matrix increases the following properties of the coating: (i) mechanical properties, such as strength, elastic modulus, hardness, and wear resistance [81,83,84], (ii) chemical properties, including corrosion resistance [62,82,83], and (iii) physical properties, e.g., high-temperature stability [79,85], or electrical and thermal conductivity [62,[86][87][88]. Among other thermal spraying techniques, CS ensures a solid state of PRMMC coatings deposition, without tensile thermal stresses, The deposition of pure ceramic particles is possible by a method similar to LPCS known as aerosol deposition (AD) [73]. The process parameters include lower working gas stagnation pressure, ambient temperature without heating and nanosized ceramic particles. As a result, lower particle velocities are obtained. Nevertheless, the deposition is possible owing to the controlled atmosphere as the process is run in a vacuum. Therefore, compared to CS, AD uses significantly lower pressure ranges, 60-1066 mbar [74]. Glosse et al. [75] analysed the influence of process parameters on DE in AD to conclude that higher chamber back pressures (10-20 mbar) decrease film thickness, despite the working gas stagnation pressure maintained in the range of 319-558 mbar. The pressure in the vacuum chamber has to be much lower than the nozzle exit pressure to produce a highly under-expanded supersonic jet. Therefore, the applied vacuum has a significant influence on the process and simultaneously preclude this procedure to be implemented for HPCS or LPCS in an air atmosphere. Furthermore, according to Glosse's results [75], increasing gas flow rates increases the kinetic energy of the impacting particles, resulting in a highly abrasive effect of particles on the coating, decreased DE, and finally thinner deposited layers. According to Hanft et al. [74] and Akedo [76], critical velocities also exist for AD and depend on the material of the ceramic particles and the substrate (Figure 4). Similar to CS of metal powder, the ceramic particles should not exceed erosion velocity, otherwise the powder will grit-blast the substrate, fracture, and bound off. Akedo [76] found that the critical velocity of nanosized (300 nm particles diameter) α-Al 2 O 3 particles was 150 m/s. It arises from small particles sizes, their agglomeration and applied vacuum. Therefore, DE depends not only on particles velocity but also on the substrate material, nature of the aerosolized particle and their distribution [73]. It appears that the same parameters are responsible for successful coating fabrication via LPCS. However, in LPCS, the stream of ceramics has to overcome the air atmosphere, which decelerates the particles, and thus requires higher velocity compared to AD. Particles velocity in LPCS can be increased by modifying the morphology of the particles. In my previous research [61], I concluded that the velocities of copper dendritic particles were much higher than spherical ones. It arises from higher drag coefficient of irregular particles [21]. Therefore, the agglomeration of ceramic particles increases the velocity of nanosized powder. What is more, nanosized agglomerated particles due to fragmentation will bond to the substrate. The methods of ceramic powder preparation for LPCS process and bonding mechanics are described in further parts of the manuscript.

Metal Matrix Composite Coatings
Particle reinforced metal matrix composite (PRMMC) coatings consist of a ductile matrix (pure metal or metal alloy) and hard reinforcement phase (different metal, ceramics, intermetallic phase, organic or inorganic material), and as a result, combine properties of both materials, e.g., resistance for high-temperature mechanical loading, maintaining increased durability [77,78]. Due to high strength, hardness, chemical inertness, high melting point, and many functional applications, ceramic powder is the most commonly selected material for reinforcement in PRMMC coatings [77,[79][80][81][82]. The uniformly distributed, coherent, and continuous hard phase in the metallic matrix increases the following properties of the coating: (i) mechanical properties, such as strength, elastic modulus, hardness, and wear resistance [81,83,84], (ii) chemical properties, including corrosion resistance [62,82,83], and (iii) physical properties, e.g., high-temperature stability [79,85], or electrical and thermal conductivity [62,[86][87][88]. Among other thermal spraying techniques, CS ensures a solid state of PRMMC coatings deposition, without tensile thermal stresses, phase transformation, decarburization, oxidation, or high porosity [28,48,89,90]. The low cost of commercially available powder mixtures and easy control of coating composition makes PRMMC coatings an attractive alternative for complex alloys.
Metal particles in CS impact the substrate with high kinetic energy and as a result undergo severe plastic deformation at a high strain rate [18,61]. Strong pressure waves interact with the expanding edge of the particle forming a jet, which is prone to localized fragmentation under a spall-like process [91]. Additionally, the temperature may increase locally in the particle boundary region and cause adiabatic shear instability [61,92]. Despite the low temperature of the process, the flow of metal and jet formation occurs. This phenomenon favours the adhesion and cohesion of the particles. What is more, the deformation is increased in PRMMC by the tamping effect of hard ceramic particles. Therefore, despite lower particles velocities obtained in LPCS, ceramic powder ensures additional work hardening of the metal particles and significantly increases the mechanical properties of the PRMMC coating.

Powders Preparation
In the CS process, PRMMC coatings are deposited as a mixture of two or more metalceramic powders. The powders mixture can be prepared by several methods illustrated in Figure 5, such as: (i) mechanical blending of powders, offering simple operation and easy control over the composition of the composite powder [82,93,94], (ii) satelliting, to improve dispersion of the small reinforcing particles by the formation of satellites on the surface of large particle of second phase [95,96], (iii) powder cladding to form a continuous and uniform metal coating on the ceramic powder and increase control of the volume fractions of the hard phase [68], (iv) mechanical ball milling to improve the distribution of reinforcement phases with control of size and content of mixed phases [97,98], (v) ball milling combined with self-propagating high-temperature synthesis or annealing in controlled atmosphere to obtain a modified structure, and (vi) spray drying to facilitate the atomisation of slurry followed by drying in hot gas, agglomeration, and sintering, which ensures homogeneous, agglomerated composite powders [99,100]. Selecting a proper mixture preparation method should be matched with matrix phase and reinforcement phase, and most importantly with mixture application. In thermal spraying processes, various powders can react differently, e.g., high temperature causes decarburization, high plastic deformation leads to a decrease of DE, etc. All the methods are compared in Figure 5 and are precisely described below.
The blending of powders is the simplest and cheapest way to prepare the mixture and various materials with a high range of particles sizes that can be used in the process. Many commercially available powders for LPCS are prepared this way, including Al-Al 2 O 3 [48,93,101] , Cu-Al 2 O 3 [62,102,103] (Figure 6), Zn-Al 2 O 3 [81,102,104], Sn-Al 2 O 3 [81,105,106], Ni-Al 2 O 3 [68,81,102], and other powder mixtures for special application, such as Cu-SiC [82,107], Al2319-TiN [108], and WC-Ni [80]. Due to their higher kinetic energy, blended powders are effectively deposited by HPCS, e.g., Al-Al 2 O 3 [109], aluminium alloys: A380-Al 2 O 3 [110,111], AA2024-Al 2 O 3 [112], Al5056-SiC [113], Cu-CuO 2 [114], and Ni-B 4 C [115]. It should be emphasised that increasing differences in the particle size, morphology, or density of mixed powders result in various ranges of particles velocities. As a result, mixed materials show divergence in DE and, in consequence, nonuniform material distribution in the deposited coating [116]. What is more, particles size range should be above 5 µm, as smaller particles decelerate in the bow shock formed above the substrate [98]. Therefore, another method was proposed, known as satelliting. In this process, two powders with various particles sizes are mixed in liquid binder [95] or lowenergy vibration mill [117,118] (Figure 6). As a result, small particles of the first phase form satellites on the surface of the second phase particles due to the action of van der Waals force. However, such a weak adhesion causes easy separation during satellite impact and usually some part of reinforcement rebounds. Al-Hamdani et al. [119] mixed Al powder (15-45 µm size range) and TiC powder (particle size < 5 µm) in a tubular mixer with the addition of a binder. Afterwards, the powder was dried at 100 • C for 12 h. Al-Hamdani et al. noticed the more evenly distributed TiC in the satellited feedstock, and subsequent more steady flow during spraying, compared to blended powders. As a result, a high proportion of ceramic that was attached to the satellited powder was embedded in the coating.  ), ball milling with SHS or annealing (lower middle) and spray drying (lower right). Blue and orange colours mean various phases. A-advantage, D-disadvantage (inspired by [98]).
The blending of powders is the simplest and cheapest way to prepare the mixture and various materials with a high range of particles sizes that can be used in the process. Many commercially available powders for LPCS are prepared this way, including Al-Al2O3 [48,93,101], Cu-Al2O3 [62,102,103] (Figure 6), Zn-Al2O3 [81,102,104], Sn-Al2O3 [81,105,106], Ni-Al2O3 [68,81,102], and other powder mixtures for special application, such as Cu-SiC [82,107], Al2319-TiN [108], and WC-Ni [80]. Due to their higher kinetic energy, blended powders are effectively deposited by HPCS, e.g., Al-Al2O3 [109], aluminium alloys: A380-Al2O3 [110,111], AA2024-Al2O3 [112], Al5056-SiC [113], Cu-CuO2 [114], and Ni-B4C [115]. It should be emphasised that increasing differences in the particle size, morphology, or density of mixed powders result in various ranges of particles velocities. As a result, mixed materials show divergence in DE and, in consequence, nonuniform material distribution in the deposited coating [116]. What is more, particles size range should be above 5 µm, as smaller particles decelerate in the bow shock formed above the substrate [98]. Therefore, another method was proposed, known as satelliting. In this process, two powders with various particles sizes are mixed in liquid binder [95] or low-energy vibration mill [117,118] (Figure 6). As a result, small particles of the first phase form satellites on the surface of the second phase particles due to the action of van der Waals force. However, such a weak adhesion causes easy separation during satellite impact and usually some part of reinforcement rebounds. Al-Hamdani et al. [119] mixed Al powder (15-45 µm size range) and TiC powder (particle size < 5 µm) in a tubular mixer with the addition of a binder. Afterwards, the powder was dried at 100 °C for 12 h. Al-Hamdani et al. noticed the more evenly distributed TiC in the satellited feedstock, and subsequent more steady flow during spraying, compared to blended powders. As a result, a high proportion of ceramic that was attached to the satellited powder was embedded in the coating.
Powder cladding can be used to increase the amount of ceramic in the coating. Within the process, the selected metal is coated on a hard phase with defined thickness to obtain a desired fraction of ceramic material [68,120]. The method is dedicated to manufacturing cladded powders and mainly includes [68]: (i) immersion coating; (ii) electroless chemical plating; (iii) electrolytic deposition; (iv) mechanical coating; (v) chemical vapor deposition (CVD); (vi) physical vapor deposition; and (vii) hydrothermal hydrogen reduction method. By selecting the appropriate process and its optimal parameters, the thickness of the coated layer can be regulated. Deposited metal works as a binder and joins particles of hard phase to agglomerates [120] (Figure 7). The process enables the deposition of a coating with a high and controlled volume fraction of the hard phase. However, CS requires a metal matrix to spray any hard particles, including ceramics. Therefore, the thickness of the clad layer should be sufficient to ensure particle adhesion [68]. It should be noted that the reinforcing phase can be cladded on the metal particles. Okimura et al. [121], to increase hard phase in the LPCS coatings, proposed the deposition of diamondlike carbon (DLC) films on the surface of Ti and Cu powders by (CVD). Meanwhile, Wang et al. [122] encapsulated aluminium powder particles with graphene to increase the corrosion resistance of the coating. Powder cladding can be used to increase the amount of ceramic in the coating. Within the process, the selected metal is coated on a hard phase with defined thickness to obtain a desired fraction of ceramic material [68,120]. The method is dedicated to manufacturing cladded powders and mainly includes [68]: (i) immersion coating; (ii) electroless chemical plating; (iii) electrolytic deposition; (iv) mechanical coating; (v) chemical vapor deposition (CVD); (vi) physical vapor deposition; and (vii) hydrothermal hydrogen reduction method. By selecting the appropriate process and its optimal parameters, the thickness of the coated layer can be regulated. Deposited metal works as a binder and joins particles of hard phase to agglomerates [120] (Figure 7). The process enables the deposition of a coating with a high and controlled volume fraction of the hard phase. However, CS requires a metal matrix to spray any hard particles, including ceramics. Therefore, the thickness of the clad layer should be sufficient to ensure particle adhesion [68]. It should be noted that the reinforcing phase can be cladded on the metal particles. Okimura et al. [121], to increase hard phase in the LPCS coatings, proposed the deposition of diamond-like carbon (DLC) films on the surface of Ti and Cu powders by (CVD). Meanwhile, Wang et al. [122] encapsulated aluminium powder particles with graphene to increase the corrosion resistance of the coating.
One effective way to increase the volume fraction of hard particles in the composite is mechanical ball milling. It solves the problem with various sized particles bonding. The process parameters (including ball-to-powder ratio, milling speed, time, and atmosphere) ensure control on the content and distribution of mixed phases and increases material uniformity [123] (Figure 8). A high energy ball mill is beneficial to the plastic deformation, work hardening, and refining of metal-ceramic composite powders into small particles, and hence improves the distribution of submicron or nanosized ceramic particles [124]. Luo et al. [125] found that the grain size of the NiCrAl matrix in the cBN-NiCrAl composite powder prepared by mechanical alloying decreased to a few tens of nanometres with increasing mechanical alloying duration ( Figure 9). However, to retain these features of powders in the as-sprayed coatings, a low-temperature process, such as cold spraying, has to be used. Salur et al. noticed that by setting milling time, the lattice strain, dislocation density and Al crystallite size can be controlled in the mixture with TiC nanoparticles (see Figure 10) [126]. Many studies reported increased coating quality and properties, such as bond strength [127] or hardness [128]. Nevertheless, the high energy of the mill produces enhanced work hardening of the ductile phase [129] or particles cold-welding into multi-agglomerates [117]. Consequently, the DE of the mixture can be decreased, and the uniformity of materials deteriorated. Therefore, this preparation method is dedicated for HPCS [128,130]. What is more, mechanical treatment can be combined with selfpropagating high-temperature synthesis (SHS) to produce fine and controlled hard phase particles in a metal matrix. Kim et al. [131] mixed in ball mill powders of Ti, B and Cu to obtain TiB 2 -43 vol.%-Cu nanocomposite powder with the ceramic particle of size 50-100 nm. The SHS reaction was uniform in the mixing powder volume due to the high thermal conductivity of copper. Neri et al. [132] coupled the SHS synthesis with high-energy ball milling to prepare nanostructured solid solutions for oxygen-sensing applications. A series of SrTi1−xFexO3−δ (STO or STFO) perovskite powders, with x ranging from 0 to 0.6 were prepared to start from SrO 2 , Ti, TiO 2 and Fe powders mixture. Based on the reported data Neri et al. concluded that the ball milling combined with SHS reaction: (i) stabilizes the formation of non-equilibrium structures; (ii) decreases the particle size, increases surface defects and hence surface reactivity; and (iii) favours the substitution of titanium by iron in the SrTiO 3 perovskite structure. Vasanthakumar et al. [133] mixed metal powders (Ti, W, Ta, M, V) in equimolar proportions and with carbon black to synthesize high entropy carbide (HEC) compact by reactive spark plasma sintering of ball milled metal-carbon elemental mixture. High-energy ball milling significantly reduced the sintering temperature of the powder. One effective way to increase the volume fraction of hard particles in the composite is mechanical ball milling. It solves the problem with various sized particles bonding. The process parameters (including ball-to-powder ratio, milling speed, time, and atmosphere) ensure control on the content and distribution of mixed phases and increases material uniformity [123] (Figure 8). A high energy ball mill is beneficial to the plastic deformation, work hardening, and refining of metal-ceramic composite powders into small particles, and hence improves the distribution of submicron or nanosized ceramic particles [124]. Luo et al. [125] found that the grain size of the NiCrAl matrix in the cBN-NiCrAl composite powder prepared by mechanical alloying decreased to a few tens of nanometres with increasing mechanical alloying duration ( Figure 9). However, to retain these features of powders in the as-sprayed coatings, a low-temperature process, such as cold spraying, has to be used. Salur et al. noticed that by setting milling time, the lattice strain, dislocation density and Al crystallite size can be controlled in the mixture with TiC nanoparticles (see Figure 10) [126]. Many studies reported increased coating quality and properties, such as bond strength [127] or hardness [128]. Nevertheless, the high energy of the mill produces enhanced work hardening of the ductile phase [129] or particles cold-welding into multiagglomerates [117]. Consequently, the DE of the mixture can be decreased, and the uniformity of materials deteriorated. Therefore, this preparation method is dedicated for HPCS [128,130]. What is more, mechanical treatment can be combined with self-propagating high-temperature synthesis (SHS) to produce fine and controlled hard phase par-        [126]. Copyright 2021 Elsevier. Figure 10. The variation of the crystallite size, lattice strain, and dislocation density of TiC/AA7075 powders estimated from XRD curves. Reprinted with permission from [126]. Copyright 2021 Elsevier.
Another method enabling the production of homogeneous nanostructured composite powder from submicron or nano-sized particles is spray drying. The process includes the following stages: (1) raw powders mixing to prepare slurry with the use of binder, (2) atomization of the slurry to fabricate composite powders and (3) heat treatment (also called calcination) of prepared powders. A wet ball milling can be used to blend the nano-sized particles homogeneously [134]. After atomization of the slurry, micro-sized nanostructured composite powders are received. However, powder morphology depends strongly on the spray drying process parameters, such as the rotating speed of nozzle, as well as inlet and outlet temperature. The final particle size and degree of sphericity of the as spay dried powders is affected by the rotating speed of the nozzle. Higher rotating speed promotes the refinement and the sphericity of the powders [134]. Afterwards, in the calcination process, organic additives are removed, and porosity is reduced. The final agglomerate grain size is usually in tens of micrometres. Kang et al. [100] used spray drying to produce 75W-25Cu wt.% nano-composite powder mixture with agglomerates size below 75 µm to achieve consistent powder feeding and a homogeneous deposit layer. It should be emphasized that spray drying enables to prepare powder dedicated to the CS process, where agglomerates are needed due to: (i) proper working of conventional powder feeder [135] and (ii) expected higher velocity to overcome bow shock formed above the substrate [100]. To increase the cohesion of agglomerated particles in cermet (e.g., WC-Co), powder sintering is suggested [136,137]. It is worth emphasising, that a major challenge in the nanosized powder mixture preparation is a uniform distribution of the ingredients, especially with a higher specific surface, e.g., carbon nanotubes (CNT) [77]. Bakhsi et al. fabricated aluminium-silicon eutectic alloy powder with an agglomerate particle size of 57 ± 21 µm containing multiwalled CNT, and they used it in atmospheric plasma spraying [99] and HPCS [138] (Figure 11). Nevertheless, to increase deposition efficiency in HPCS, spray dried powder was mixed with pure Al powder. Another method enabling the production of homogeneous nanostructured composite powder from submicron or nano-sized particles is spray drying. The process includes the following stages: (1) raw powders mixing to prepare slurry with the use of binder, (2) atomization of the slurry to fabricate composite powders and (3) heat treatment (also called calcination) of prepared powders. A wet ball milling can be used to blend the nanosized particles homogeneously [134]. After atomization of the slurry, micro-sized nanostructured composite powders are received. However, powder morphology depends strongly on the spray drying process parameters, such as the rotating speed of nozzle, as well as inlet and outlet temperature. The final particle size and degree of sphericity of the as spay dried powders is affected by the rotating speed of the nozzle. Higher rotating speed promotes the refinement and the sphericity of the powders [134]. Afterwards, in the calcination process, organic additives are removed, and porosity is reduced. The final agglomerate grain size is usually in tens of micrometres. Kang et al. [100] used spray drying to produce 75W-25Cu wt.% nano-composite powder mixture with agglomerates size below 75 µm to achieve consistent powder feeding and a homogeneous deposit layer. It should be emphasized that spray drying enables to prepare powder dedicated to the CS process, where agglomerates are needed due to: (i) proper working of conventional powder feeder [135] and (ii) expected higher velocity to overcome bow shock formed above the substrate [100]. To increase the cohesion of agglomerated particles in cermet (e.g., WC-Co), powder sintering is suggested [136,137]. It is worth emphasising, that a major challenge in the nanosized powder mixture preparation is a uniform distribution of the ingredients, especially with a higher specific surface, e.g., carbon nanotubes (CNT) [77]. Bakhsi et al. fabricated aluminium-silicon eutectic alloy powder with an agglomerate particle size of 57 ± 21 µm containing multiwalled CNT, and they used it in atmospheric plasma spraying [99] and HPCS [138] (Figure 11). Nevertheless, to increase deposition efficiency in HPCS, spray dried powder was mixed with pure Al powder.

LPCS PRMMC Coatings Applications
PRMMC LPCS coatings combine various materials, resulting in advisable properties, e.g., good wear behaviour and increased fatigue strength, a high thermal conductivity combined with an increased creep resistance, great creep and corrosion resistance at high temperatures, as well as coupled high electrical conductivity and mechanical resistance [65].
The role of hard phase in metal-ceramic composites usually is played by ceramic powders, such as Al2O3 [48,101,109,111,112,140], SiC [82,107,108,113,154], B4C [115,146], WC [80,146,147] TiC [126,146]. The plastic deformation of impacting metallic particles is responsible for ceramic deposition due to mechanical interlocking in ductile metal. The high content (e.g., 50 wt.%) of coarse ceramic admixture (e.g., −30 µm) in initial powder significantly increases the probability of particles collision, fracturing and bouncing off. Consequently, more than 80 vol.% of the ceramic powder included in the mixtures usually rebounds, decreasing the volume of ceramics in the coating [62]. To increase ceramic content in the coating, the higher mass of ceramic powder should be mixed with metal. Melendez and McDonald [63] obtained 52 vol.% of WC particles in WC + Ni coating deposited with the use of 96 wt.% WC + 4 wt.% Ni powder blend mixture. The powder preparation method is meaningful as well. Feng et al. [115] mechanically blended Ni with B4C in various proportions. However, the ceramic content was always less than 20 vol.%. By powder cladding with the use of the CVD method, Feng et al. obtained a much higher deposition efficiency of B4C particles in the cold spray coatings. Ceramic content in the coating reached 44.0 vol.% for the NiCVD-87 vol.% B4C powder mixture. In one of my research [68], I coated Al2O3 with Ni to increase alumina content in the coating and to avoid the fracture of ceramic particles. As a result, the ceramic contribution in the coating sprayed with mechanically blended commercial Ni-Al2O3 and Ni coated Al2O3 increased Figure 11. SEM micrographs of the spray-dried (SD) spherical agglomerates of SD Al-5CNT (a) and SD Al-10CNT powder (b), the outer surface of a single SD Al-5CNT powder (c), inside view of fractured SD Al-5CNT powder (d), the outer surface of a single SD Al-10CNT powder (e), and inside view of fractured SD Al-10CNT powder (f). Inset of (a) and (b) shows the powder size distribution. Reprinted with permission from [138]. Copyright 2009 Elsevier.

LPCS PRMMC Coatings Applications
PRMMC LPCS coatings combine various materials, resulting in advisable properties, e.g., good wear behaviour and increased fatigue strength, a high thermal conductivity combined with an increased creep resistance, great creep and corrosion resistance at high temperatures, as well as coupled high electrical conductivity and mechanical resistance [65].
The role of hard phase in metal-ceramic composites usually is played by ceramic powders, such as Al 2 O 3 [48,101,109,111,112,140], SiC [82,107,108,113,154], B 4 C [115,146], WC [80,146,147] TiC [126,146]. The plastic deformation of impacting metallic particles is responsible for ceramic deposition due to mechanical interlocking in ductile metal. The high content (e.g., 50 wt.%) of coarse ceramic admixture (e.g., −30 µm) in initial powder significantly increases the probability of particles collision, fracturing and bouncing off. Consequently, more than 80 vol.% of the ceramic powder included in the mixtures usually rebounds, decreasing the volume of ceramics in the coating [62]. To increase ceramic content in the coating, the higher mass of ceramic powder should be mixed with metal. The conditions of LPCS make the process attractive for many applications. Previously, as a portable unit with a handy spraying gun, it was employed first of all for structural, dimensional, or functional restoration, and since the nozzle exit diameter is 5 mm, the work is precise without any additional masking. A good coating's machinability ensures high surface quality with the possibility of on-site repair [64]. What is more, the method can be adapted to the recycling process and elongating selected products' life cycle. In the field of art, LPCS can be applied as decoration of various panel natures including glass, rusty sheets of iron, copper plates. Different metal-ceramic feedstock powders are explored as paintwork due to possible metal colour mixing and surface topography modifications. Further applications of LPCS depend on the expected functionality and include mostly coatings with high electrical conductivity [103,145], electrochemical corrosion resistance [62,83,102,105], high-temperature corrosion resistance [155,156], wear resistance [79,157,158], solid lubrication [121,159], interlayers in welding or soldering processes [160,161], etc. The high quality of the coating and its properties arise from ceramic addition, which significantly reduces the porosity and increases the contact surface area of metal particles [122,162].
LPCS ensures uniform distribution of ingredients in dense PRMMC composite coatings and as a result high electrical conductivity and corrosion resistance. According to my previous research [62], ceramic admixture increases the surface contact between copper particles due to plastic deformation and as a result electrical conductivity up to 62.5% IACS. A further increase in electrical conductivity is possible due to the PSHT of the coating (Figure 13a) [62,145]. It should be noted that dense Cu-Al2O3 coatings with low porosity exhibit high electrical conductivity (about 90% of initial value) after salt-spray and Kesternich corrosion tests [82]. Moreover, copper-alumina composite coatings can The conditions of LPCS make the process attractive for many applications. Previously, as a portable unit with a handy spraying gun, it was employed first of all for structural, dimensional, or functional restoration, and since the nozzle exit diameter is 5 mm, the work is precise without any additional masking. A good coating's machinability ensures high surface quality with the possibility of on-site repair [64]. What is more, the method can be adapted to the recycling process and elongating selected products' life cycle. In the field of art, LPCS can be applied as decoration of various panel natures including glass, rusty sheets of iron, copper plates. Different metal-ceramic feedstock powders are explored as paintwork due to possible metal colour mixing and surface topography modifications. Further applications of LPCS depend on the expected functionality and include mostly coatings with high electrical conductivity [103,145], electrochemical corrosion resistance [62,83,102,105], high-temperature corrosion resistance [155,156], wear resistance [79,157,158], solid lubrication [121,159], interlayers in welding or soldering processes [160,161], etc. The high quality of the coating and its properties arise from ceramic addition, which significantly reduces the porosity and increases the contact surface area of metal particles [122,162].
LPCS ensures uniform distribution of ingredients in dense PRMMC composite coatings and as a result high electrical conductivity and corrosion resistance. According to my previous research [62], ceramic admixture increases the surface contact between copper particles due to plastic deformation and as a result electrical conductivity up to 62.5% IACS. A further increase in electrical conductivity is possible due to the PSHT of the coating (Figure 13a) [62,145]. It should be noted that dense Cu-Al 2 O 3 coatings with low porosity exhibit high electrical conductivity (about 90% of initial value) after salt-spray and Kesternich corrosion tests [82]. Moreover, copper-alumina composite coatings can significantly increase the corrosion potential of aluminium busbars due to the reduction of porosity and densification of the coating [62] (Figure 13b). Dzhurinsky et al. [163] examined aluminium, aluminium-alumina and aluminium-zinc-alumina coatings and demonstrated by accelerated corrosion test that corrosion of the sprayed composites intensified as the concentration of alumina particles increased within the coating. Wang et al. [162] tested by HPCS deposition of Al 5056-SiC mixture and concluded that SiC particles crack due to high-velocity impact and provide passage for electrolyte through inter-particle boundaries intensifying corrosion progress. On the other hand, Bai et al. [104] showed that the presence of Zn elements played a role in sacrificial anodic protection in Zn-Ni composite coatings and ensured higher corrosion resistance compared to pure zinc coatings. Therefore, the composite mixture should be matched to the designed application. al. [162] tested by HPCS deposition of Al 5056-SiC mixture and concluded that SiC particles crack due to high-velocity impact and provide passage for electrolyte through interparticle boundaries intensifying corrosion progress. On the other hand, Bai et al. [104] showed that the presence of Zn elements played a role in sacrificial anodic protection in Zn-Ni composite coatings and ensured higher corrosion resistance compared to pure zinc coatings. Therefore, the composite mixture should be matched to the designed application.
(a) (b) High-temperature corrosion-resistant coatings by CS are usually sprayed with the use of HPCS units [164][165][166]. The commonly applied powder material is Ni-based superalloy with chromium admixture, which has to block the penetration of corrosive species toward the substrate. Kilicay [156] applied Ni-Zn-Al2O3 to spray MMC coating on TZM alloy by LPCS. Kilicay chose Ni and Zn, which are very prone to oxidation and formed NiO and ZnO films on the coating surface. As a result, coating prevented contact of oxygen to the titanium-zirconium-molybdenum (TZM) alloy by the reaction of Ni and Zn with oxygen at high temperatures of 900 °C. The Al2O3 was chosen to densify the coating and improve coating adhesion. The specific mass changes of the TZM substrate and MMC coating at high temperature and air atmosphere is shown in Figure 14a. The mass of the TZM alloy sharply decreased by forming MoO3 oxide layers at temperatures above 600 °C due to the evaporation mechanism. The results showed that the Ni-Zn-Al2O3 MMC coating exhibited a remarkable oxidation resistance on the TZM alloy at the test temperatures. It is thus an interesting alternative for hot corrosion resistant superalloys coating, which was shown, e.g., by Zhang et al. [165] for CoNiCrAlY deposited with LPCS. High-temperature corrosion-resistant coatings by CS are usually sprayed with the use of HPCS units [164][165][166]. The commonly applied powder material is Ni-based superalloy with chromium admixture, which has to block the penetration of corrosive species toward the substrate. Kilicay [156] applied Ni-Zn-Al 2 O 3 to spray MMC coating on TZM alloy by LPCS. Kilicay chose Ni and Zn, which are very prone to oxidation and formed NiO and ZnO films on the coating surface. As a result, coating prevented contact of oxygen to the titanium-zirconium-molybdenum (TZM) alloy by the reaction of Ni and Zn with oxygen at high temperatures of 900 • C. The Al 2 O 3 was chosen to densify the coating and improve coating adhesion. The specific mass changes of the TZM substrate and MMC coating at high temperature and air atmosphere is shown in Figure 14a. The mass of the TZM alloy sharply decreased by forming MoO 3 oxide layers at temperatures above 600 • C due to the evaporation mechanism. The results showed that the Ni-Zn-Al 2 O 3 MMC coating exhibited a remarkable oxidation resistance on the TZM alloy at the test temperatures. It is thus an interesting alternative for hot corrosion resistant superalloys coating, which was shown, e.g., by Zhang et al. [165] for CoNiCrAlY deposited with LPCS. The wear resistance of the coating is highly influenced by MMC composition. The most popular LPCS process mixtures (Al/Al2O3 and Cu/Al2O3) presents a relatively high coefficient of friction (COF) of 0.764 [84] and 0.88 [102], respectively. An optimization of spraying process parameters can decrease the COF value. For instance, Szala et al. [84] reported the COF of 0.555. What is more, Szala et al. obtained in the wear tests a superior slide wear resistance of Cu/Al2O3 coating K = 7.41 × 10 −7 mm 3 ·N −1 ·m −1 . Wear resistance should be regulated by the content of the ceramic powder admixture. Chen et al. [143] examined the CuSn5-Al2O3 mixture and noticed that the wear rate of coatings decreases with the increase of Al2O3 content (up to 30 wt.%) and obtained very satisfactory results (see Figure 14b). Lee et al. [146] sprayed Ni mechanically blended with B4C, TiC and WC and analysed the effect of carbide particle momentum on coatings wear resistance. By the applied mathematical model Lee et al. showed that the momentum of WC particles was significantly higher compared to the other ceramic powder particles. Consequently, WC particles increased the level of work hardening of the nickel matrix. What is more, due to the higher fracture toughness of large WC (size of 36 ± 11 µm) particles and increased work hardening of Ni, the WC-Ni MMC coatings showed the lowest wear resistance. The proportion of metal-ceramic powders in PRMMC has a significant influence on the wear resistance of the coating. This statement was proven by Melendez et al. [147] who blended nickel with various contents of WC and showed that the wear rate of the coatings decreased significantly as the mean free path between the agglomerated WC particles decreased. The highest wear resistance, comparable to high-velocity oxygen fuel (HVOF) and HPCS WC-based coatings, Melendez et al. obtained for WC-Ni (96-4 wt.%) powder mixture, resulting in a 66-44 wt.% coating (Figure 15a). Furthermore, high ceramic content in PRMMC can promote other applications, such as steam reforming, which requires a catalyst with support. A popular couple would be nickel catalysts with alumina as support. The activity of the nickel-based catalyst is affected by the reduction degree of nickel species [167], while the alumina support is affected by a high specific surface area, providing a high dispersion of the metallic phase [168]. To assure high ceramic content, I sprayed by LPCS nickel-cladded alumina powder and obtained the coating with Al2O3 up to 30.5 wt% [68]. The wear resistance of the coating is highly influenced by MMC composition. The most popular LPCS process mixtures (Al/Al 2 O 3 and Cu/Al 2 O 3 ) presents a relatively high coefficient of friction (COF) of 0.764 [84] and 0.88 [102], respectively. An optimization of spraying process parameters can decrease the COF value. For instance, Szala et al. [84] reported the COF of 0.555. What is more, Szala et al. obtained in the wear tests a superior slide wear resistance of Cu/Al 2 O 3 coating K = 7.41 × 10 −7 mm 3 ·N −1 ·m −1 . Wear resistance should be regulated by the content of the ceramic powder admixture. Chen et al. [143] examined the CuSn5-Al 2 O 3 mixture and noticed that the wear rate of coatings decreases with the increase of Al 2 O 3 content (up to 30 wt.%) and obtained very satisfactory results (see Figure 14b). Lee et al. [146] sprayed Ni mechanically blended with B 4 C, TiC and WC and analysed the effect of carbide particle momentum on coatings wear resistance. By the applied mathematical model Lee et al. showed that the momentum of WC particles was significantly higher compared to the other ceramic powder particles. Consequently, WC particles increased the level of work hardening of the nickel matrix. What is more, due to the higher fracture toughness of large WC (size of 36 ± 11 µm) particles and increased work hardening of Ni, the WC-Ni MMC coatings showed the lowest wear resistance. The proportion of metal-ceramic powders in PRMMC has a significant influence on the wear resistance of the coating. This statement was proven by Melendez et al. [147] who blended nickel with various contents of WC and showed that the wear rate of the coatings decreased significantly as the mean free path between the agglomerated WC particles decreased. The highest wear resistance, comparable to high-velocity oxygen fuel (HVOF) and HPCS WC-based coatings, Melendez et al. obtained for WC-Ni (96-4 wt.%) powder mixture, resulting in a 66-44 wt.% coating (Figure 15a). Furthermore, high ceramic content in PRMMC can promote other applications, such as steam reforming, which requires a catalyst with support. A popular couple would be nickel catalysts with alumina as support. The activity of the nickel-based catalyst is affected by the reduction degree of nickel species [167], while the alumina support is affected by a high specific surface area, providing a high dispersion of the metallic phase [168]. To assure high ceramic content, I sprayed by LPCS nickel-cladded alumina powder and obtained the coating with Al 2 O 3 up to 30.5 wt% [68]. from [147]. Copyright 2013 Elsevier.) and COF curves of (Cu-5Sn)/Al2O3-Ag coatings with various Ag content (0-20 wt.%) (b) (Reprinted with permission from [142]. Copyright 2020 Elsevier).
A great opportunity to decrease the COF gives the application of solid-lubricating coating. The most popular material is a mixture of metal [159,169] or metal-ceramic [170] powders with graphite powder. Okimura et al. [121] coated Cu spherical particles with diamond-like carbon (DLC) by CVD method for further usage in the LPCS process and concluded that the Cu-DLC composite coatings deposited from thin DLC-coated Cu particles behaved like a solid lubricant in the ball-on-disk tests. For the protection of moving parts in seawater conditions, Chen et al. [142] applied to silver in the metal-ceramic mixture and sprayed (Cu-5Sn)/Al2O3-Ag solid-lubricating LPCS MMC coating. Silver, similar to graphite, presents low friction and wear in artificial seawater environments. Via the controlled addition of silver powder, up to 20 wt.% Ag, the COF of the coatings was significantly decreased (Figure 15b).
The LPCS can also solve the difficulties of joining materials with low weldability. Due to significant differences in physical and chemical properties, such as melting and boiling temperature, coefficient of thermal and electrical conductivity, an oxide layer, the limited mutual solubility resulting in heterogeneous solutions at room temperature, thermal expansion mismatch, and suitability at higher temperatures, dissimilar materials show low bond strength [171][172][173]. As a result, the formation of bulky and directional intermetallic compounds detrimental to the joint occurs [173][174][175]. Among various joined construction materials, aluminium and steel are very popular. However, the resistance spot welding (RSW) joint of these metals is characterised by reduced mechanical properties resulting from the brittle intermetallic phases [176,177]. To prevent the formation of the hard phases, a smooth transition zone between two different metals by an intermediate layer can be obtained [177][178][179][180][181]. Nevertheless, most of the applied methods are based on large-area coating. LPCS enables coating a precise area of the material before welding. Analysing the material for the aluminium-steel intermediate layer I proposed free materials: Al-Al2O3, Ni-Al2O3 and Al-Ni-Al2O3 to analyse the formation of advisable Al-Ni intermetallic phases inside the coating [160]. Nevertheless, Ni-Al2O3 interlayer showed after welding the most uniform microstructure and as a result, the highest shear strength comparable with the aluminium + aluminium joints (Table 2). Furthermore, the fracture out of the welding nugget zone indicated a higher strength of joint than the aluminium base material. Wojdat et al. [161] applied multi-layered coatings as an interlayer in the soldering process of aluminium alloy to graphite. The graphite was coated by soft aluminium, then densified by Al-Al2O3, to be finally sprayed by copper coating. The aluminium alloy was coated by copper as well and soldered by tin to multi-layered graphite. The metallic (e.g., Al and Cu) and PRMMC (e.g., Al-Al2O3 and Cu-Al2O3) composites, LPCS interlayers effectively limits formation of the reaction zones in soldering process and improves the Figure 15. Curve of wear rate versus mean free path for various WC-Ni composite coatings (a) (Reprinted with permission from [147]. Copyright 2013 Elsevier.) and COF curves of (Cu-5Sn)/Al 2 O 3 -Ag coatings with various Ag content (0-20 wt.%) (b) (Reprinted with permission from [142]. Copyright 2020 Elsevier).
A great opportunity to decrease the COF gives the application of solid-lubricating coating. The most popular material is a mixture of metal [159,169] or metal-ceramic [170] powders with graphite powder. Okimura et al. [121] coated Cu spherical particles with diamond-like carbon (DLC) by CVD method for further usage in the LPCS process and concluded that the Cu-DLC composite coatings deposited from thin DLC-coated Cu particles behaved like a solid lubricant in the ball-on-disk tests. For the protection of moving parts in seawater conditions, Chen et al. [142] applied to silver in the metal-ceramic mixture and sprayed (Cu-5Sn)/Al 2 O 3 -Ag solid-lubricating LPCS MMC coating. Silver, similar to graphite, presents low friction and wear in artificial seawater environments. Via the controlled addition of silver powder, up to 20 wt.% Ag, the COF of the coatings was significantly decreased (Figure 15b).
The LPCS can also solve the difficulties of joining materials with low weldability. Due to significant differences in physical and chemical properties, such as melting and boiling temperature, coefficient of thermal and electrical conductivity, an oxide layer, the limited mutual solubility resulting in heterogeneous solutions at room temperature, thermal expansion mismatch, and suitability at higher temperatures, dissimilar materials show low bond strength [171][172][173]. As a result, the formation of bulky and directional intermetallic compounds detrimental to the joint occurs [173][174][175]. Among various joined construction materials, aluminium and steel are very popular. However, the resistance spot welding (RSW) joint of these metals is characterised by reduced mechanical properties resulting from the brittle intermetallic phases [176,177]. To prevent the formation of the hard phases, a smooth transition zone between two different metals by an intermediate layer can be obtained [177][178][179][180][181]. Nevertheless, most of the applied methods are based on large-area coating. LPCS enables coating a precise area of the material before welding. Analysing the material for the aluminium-steel intermediate layer I proposed free materials: Al-Al 2 O 3 , Ni-Al 2 O 3 and Al-Ni-Al 2 O 3 to analyse the formation of advisable Al-Ni intermetallic phases inside the coating [160]. Nevertheless, Ni-Al 2 O 3 interlayer showed after welding the most uniform microstructure and as a result, the highest shear strength comparable with the aluminium + aluminium joints (Table 2). Furthermore, the fracture out of the welding nugget zone indicated a higher strength of joint than the aluminium base material. Wojdat et al. [161] applied multi-layered coatings as an interlayer in the soldering process of aluminium alloy to graphite. The graphite was coated by soft aluminium, then densified by Al-Al 2 O 3 , to be finally sprayed by copper coating. The aluminium alloy was coated by copper as well and soldered by tin to multi-layered graphite. The metallic (e.g., Al and Cu) and PRMMC (e.g., Al-Al 2 O 3 and Cu-Al 2 O 3 ) composites, LPCS interlayers effectively limits formation of the reaction zones in soldering process and improves the mechanical properties of the joint [182]. It is worth emphasising that pure metal coatings are better intermediate layers in the soldering process [182][183][184][185]. Nevertheless, ceramic particles present on the LPCS coating surface limit soldering properties, such as the wettability of the composite interlayer with Zn-Al solder, which eliminates the use of Al-Al 2 O 3 powder in the soldering process [183]. The LPCS can be combined with a magnetron sputtering (MS) process to produce transparent and conductive thin films. The MS can be used to deposit a variety of materials. Nevertheless, some ceramic coatings (e.g., indium-tin-oxide (ITO)) requires ceramic or metallic feedstock, called target. The ceramic In 2 O 3 -SnO 2 sinter provides higher performance and thus is more frequently applied than metallic In-Sn. Nevertheless, the sinters are soldered to the copper carrier disk and show a tendency to wrap or crack due to differences in thermal expansion coefficient [186,187]. To solve this problem, I produced a composite Sn-In 2 O 3 target by LPCS coating [117,118]. Due to the oxidation of Sn before spraying, an additional SnO phase was obtained in the coating. Deposited LPCS coatings showed mean thickens of 1 mm with uniform distribution of indium oxide and tin particles. Finally, high-quality ITO transparent thin films on glass substrate were obtained in the MS process, with the highest transmission of 88% at λ = 550 nm and the lowest resistivity of 0.03 Ω·cm.
Functional graded PRMMCs coatings can be sprayed by LPCS as well. As shown in one of my previous papers [103], the 3 mm thick Al-Al 2 O 3 coating on steel substrate had microhardness variations through the thickness from 83.7 HV0.3 next to the substrate up to 129.5 HV0.3 in the top part ( Figure 16). It arose from the thermal recovery of the aluminium in the lower part of the composite coating as multi-layered spraying of thick coating. In this way, the coating gained high hardness on the surface while being ductile at the coating/substrate interface. Adebiyi et al. [154] sprayed a mixture of Ti-6Al-4V with SiC powder by LPCS process. Deposited coatings were free of phase transformations, decarburization, or decompositions. The high impact of the blend resulted in microstraining, amorphization, and grain refinement. The hardness was improved from 291 ± 13.9 HV0.3 in the substrate to 652 ± 12.7 HV0.3 in the coating due to the partially homogeneous distribution of SiC. What is more, the hardness and other mechanical properties can be increased by using nanostructured coatings, deposited by nano-sized powders [188]. The LPCS can be coupled with laser [65,[189][190][191][192] or friction stir processing (FSP) [193][194][195][196][197] treatment to improve structure of as-sprayed coating. In a laser-assisted lowpressure cold spraying (LALPCS) process the cold spray spot interacts with the laser irradiation on the substrate and as a result, local temperature rises ( Figure 17). Kulmala et al. [65] used LALPCS to spray copper-alumina and nickel-alumina coatings and found that laser irradiation increased deposition efficiency and densification of the coatings. Moreover, copper-alumina coating open cell potential was near bulk potential ( Figure 18a). Another surface modification technique, friction stir processing (FPS), shows great capability in improving materials structures, quality, and preparing the surface of metal-matrix composites [195][196][197] (Figure 19). Hodder et al. [198] applied friction stir processing to modify as-sprayed LPCS Al-Al2O3 and found that the particle mean free path decreased significantly due to the re-distribution of the Al2O3 particles trapped within the Al matrix, and consequently increased load share and microhardness values. Khodabakhshi et al. [199] fabricated a dense titanium coating with refined grain structure by combining cold spraying and FSP. The optimization of the plunge depth of the FSP head resulted in compressive residual stresses with a maximum negative value of around 400 MPa at the advancing side. What is more, Khodabakhshi et al. concluded in another research [200] that the bonding mechanism between aluminium substrate and titanium particles in CS was reinforced by a chemical bonding. Due to material mixing and deformation, the solid-state chemical inter-diffusion of elements occurred during FSP (Figure 18b). Consequently, the Al3Ti intermetallic layer with a thickness of ~10-20 nm formed inducing nano-scale interfacial chemical bonding. The formation of intermetallic phases that increase hardness of the coating is possible by conventional PSHT of the coating in the furnace. In this case two reactive metal powders (e.g., Al and Ni) should be mechanically blended and LPCS sprayed. Nevertheless, high porosity forms in the coating. To eliminate the porosity, I proposed resistance spot welder (RSW) heat treatment with simultaneous compression of the electrodes [153]. As a result, the porosity of the coating decreased from 20.8% to 4.6% in conventionally and RSW heat-treated coatings, respectively. Table 3 shows the main applications of PRMMC coatings produced by LPCS. The LPCS can be coupled with laser [65,[189][190][191][192] or friction stir processing (FSP) [193][194][195][196][197] treatment to improve structure of as-sprayed coating. In a laser-assisted low-pressure cold spraying (LALPCS) process the cold spray spot interacts with the laser irradiation on the substrate and as a result, local temperature rises ( Figure 17). Kulmala et al. [65] used LALPCS to spray copper-alumina and nickel-alumina coatings and found that laser irradiation increased deposition efficiency and densification of the coatings. Moreover, copper-alumina coating open cell potential was near bulk potential ( Figure 18a). Another surface modification technique, friction stir processing (FPS), shows great capability in improving materials structures, quality, and preparing the surface of metal-matrix composites [195][196][197] (Figure 19). Hodder et al. [198] applied friction stir processing to modify as-sprayed LPCS Al-Al 2 O 3 and found that the particle mean free path decreased significantly due to the re-distribution of the Al 2 O 3 particles trapped within the Al matrix, and consequently increased load share and microhardness values. Khodabakhshi et al. [199] fabricated a dense titanium coating with refined grain structure by combining cold spraying and FSP. The optimization of the plunge depth of the FSP head resulted in compressive residual stresses with a maximum negative value of around 400 MPa at the advancing side. What is more, Khodabakhshi et al. concluded in another research [200] that the bonding mechanism between aluminium substrate and titanium particles in CS was reinforced by a chemical bonding. Due to material mixing and deformation, the solid-state chemical inter-diffusion of elements occurred during FSP (Figure 18b). Consequently, the Al 3 Ti intermetallic layer with a thickness of~10-20 nm formed inducing nano-scale interfacial chemical bonding. The formation of intermetallic phases that increase hardness of the coating is possible by conventional PSHT of the coating in the furnace. In this case two reactive metal powders (e.g., Al and Ni) should be mechanically blended and LPCS sprayed. Nevertheless, high porosity forms in the coating. To eliminate the porosity, I proposed resistance spot welder (RSW) heat treatment with simultaneous compression of the electrodes [153]. As a result, the porosity of the coating decreased from 20.8% to 4.6% in conventionally and RSW heat-treated coatings, respectively. Table 3 shows the main applications of PRMMC coatings produced by LPCS.

LPCS All-Ceramic Coatings
Ceramic materials are characterized by more complex structures than metals. The ionic and covalent bonding assures high strength and hardness, low thermal conductivity, or chemical inertness characteristics [201], and thus these are common and versatile types of coating applied in thermal spraying processes. Various compositions of ceramic materials (fed separately or as a mixture) form coatings applied as active layers to improve optoelectronic, photocatalysis, biocompatibility and mechanical properties such as hardness, friction, abrasion resistance, thermal and electrical insulation, corrosion resistance, and thus increase the lifetime of coated parts [202]. In the wide group of processes dedicated to ceramic coatings deposition, thermal spraying stands out due to: (i) unlimited substrate dimensions and complex shapes, (ii) stable stoichiometry of the material, (iii) high deposition efficiency, (iv) low operation costs and the most important high range of coating's thickness, from hundreds of nanometres to several millimetres [203]. The capability to deposit thick ceramic coatings is another crucial advantage to protect the substrate from premature degradation as a result of wear [204,205], corrosion [206,207] or high-temperature [208,209], etc.
However, in the conventional thermal spray processes (e.g., atmospheric plasma spraying or high-velocity oxygen fuel) the high process temperature leads to a melting of the applied material or its intensive heating with a heat source. As a result, a change in particle shape, an increase in powder particle size, phase transitions (e.g., anatase to rutile, which is less photocatalytically active), structural modification or technological defects such as porosity or micro-cracks are generated [210][211][212][213][214]. Eventually, the melted particles lose the characteristics and properties of the nanostructured material. Therefore, low-temperature, kinetic-based processes are sought to improve the coating's quality and fill the gap. LPCS and its vacuum modification AD are the most promising methods. The coatings deposition in these techniques relies on the mechanical interlocking and adhesion of the fine particles resulting in: (i) unmodified feedstock phase composition, (ii) undamaged Figure 19. Schematic implementation of FSP on the surface of CS titanium coating (a), top-view macro-image from the prepared coating layers after two-steps cold gas spraying and friction-stirring showing the measurement profiles for residual stress (b), FE-SEM images (c,d) and optical microstructures (e,f) from the porous CS sprayed titanium (d,f) coating and (d,f) friction-stirred one, respectively, indentation Vickers micro-hardness profile close to the surface of produced modified coating layer (g). Reprinted with permission from [199]. Copyright 2019 Elsevier.

LPCS All-Ceramic Coatings
Ceramic materials are characterized by more complex structures than metals. The ionic and covalent bonding assures high strength and hardness, low thermal conductivity, or chemical inertness characteristics [201], and thus these are common and versatile types of coating applied in thermal spraying processes. Various compositions of ceramic materials (fed separately or as a mixture) form coatings applied as active layers to improve optoelectronic, photocatalysis, biocompatibility and mechanical properties such as hardness, friction, abrasion resistance, thermal and electrical insulation, corrosion resistance, and thus increase the lifetime of coated parts [202]. In the wide group of processes dedicated to ceramic coatings deposition, thermal spraying stands out due to: (i) unlimited substrate dimensions and complex shapes, (ii) stable stoichiometry of the material, (iii) high deposition efficiency, (iv) low operation costs and the most important high range of coating's thickness, from hundreds of nanometres to several millimetres [203]. The capability to deposit thick ceramic coatings is another crucial advantage to protect the substrate from premature degradation as a result of wear [204,205], corrosion [206,207] or high-temperature [208,209], etc.
However, in the conventional thermal spray processes (e.g., atmospheric plasma spraying or high-velocity oxygen fuel) the high process temperature leads to a melting of the applied material or its intensive heating with a heat source. As a result, a change in particle shape, an increase in powder particle size, phase transitions (e.g., anatase to rutile, which is less photocatalytically active), structural modification or technological defects such as porosity or micro-cracks are generated [210][211][212][213][214]. Eventually, the melted particles lose the characteristics and properties of the nanostructured material. Therefore, low-temperature, kinetic-based processes are sought to improve the coating's quality and fill the gap. LPCS and its vacuum modification AD are the most promising methods.
The coatings deposition in these techniques relies on the mechanical interlocking and adhesion of the fine particles resulting in: (i) unmodified feedstock phase composition, (ii) undamaged substrate from input heat, and (iii) dense layer with unaffected powder properties [73]. Both methods enable efficient ceramic spraying. However, a proper powder preparation is needed.

Powders Preparation
The bonding mechanism of metallic particles in LPCS is attributed to plastic deformation at a high strain rate. The impacting metal particles show the highest shear strain at the particle's interface [215,216]. In contrast, the mechanism with plastic and features of inelastic deformation may occur for ceramics. However, fine particles have to be applied in the deposition process [39,40]. What is more, due to high-velocity ceramic particle impact, a shear strain spreads as a shear cone towards the particle centre and the maximum is obtained inside the particle. Therefore, the strain distribution in AD is much less localized than that of LPCS. Particles impact simulations performed by Daneshian et al. [40] revealed three different impact behaviours in the AD process: (i) rebounding, (ii) bonding and (iii) fragmentation. However, bonding occurred only for small particles of 25-75 nm, while particles larger than 75 nm were fragmented and rebound ( Figure 20). It should be noted that LCPS operates at higher pressures than in AD due to the ambient atmosphere, and thus generates the bow shock in front of the substrate decelerating the particles. This phenomenon limits the application of fine ceramic particles in LPCS, as the particles would not reach the substrate. There are several requirements for powder preparation to spray ceramic particles by CS [74]: (i) nanosized particles should be agglomerated to min. 15 µm in diameter to pass through the shockwave, (ii) the agglomerates should be porous, and (iii) they should have structures with a continuous epitaxial-like crystal array across a plurality of primary particles, so that the particles can be easily fragmented and adhere during impact. substrate from input heat, and (iii) dense layer with unaffected powder properties [73]. Both methods enable efficient ceramic spraying. However, a proper powder preparation is needed.

Powders Preparation
The bonding mechanism of metallic particles in LPCS is attributed to plastic deformation at a high strain rate. The impacting metal particles show the highest shear strain at the particle's interface [215,216]. In contrast, the mechanism with plastic and features of inelastic deformation may occur for ceramics. However, fine particles have to be applied in the deposition process [39,40]. What is more, due to high-velocity ceramic particle impact, a shear strain spreads as a shear cone towards the particle centre and the maximum is obtained inside the particle. Therefore, the strain distribution in AD is much less localized than that of LPCS. Particles impact simulations performed by Daneshian et al. [40] revealed three different impact behaviours in the AD process: (i) rebounding, (ii) bonding and (iii) fragmentation. However, bonding occurred only for small particles of 25-75 nm, while particles larger than 75 nm were fragmented and rebound ( Figure 20). It should be noted that LCPS operates at higher pressures than in AD due to the ambient atmosphere, and thus generates the bow shock in front of the substrate decelerating the particles. This phenomenon limits the application of fine ceramic particles in LPCS, as the particles would not reach the substrate. There are several requirements for powder preparation to spray ceramic particles by CS [74]: (i) nanosized particles should be agglomerated to min. 15 µm in diameter to pass through the shockwave, (ii) the agglomerates should be porous, and (iii) they should have structures with a continuous epitaxial-like crystal array across a plurality of primary particles, so that the particles can be easily fragmented and adhere during impact.  The phenomena present during the deposition of ceramic particles by AD are similar to those occurring during LPCS. Hanft et al. [73] divided particles by the size and stage of agglomeration and described possible processes in AD (see Figure 21a). The ceramic particles size ready to bond is in the range of 200 nm-2 µm at intermediate energies. As the submicron particle strikes the substrate, cracks form by whole volume and fragmentation occurs due to impact pressure. Further moving or rotating of the fragments provides arrangement and densification. Upcoming particles cause rebinding of fragments, further plastic deformation and consolidation of the deposited material. The plasticity is described by quasi-static compression and respectively determined thresholds for plasticity [217]. Ceramic agglomerates impact the substrate and due to the kinetic energy get separated into fragments. The coating formation is possible, however the quality can be worsened. Large agglomerates will erode the substrate and rebound. The coating formation can be divided according to Figure 21b into stage (1), which concerns particles impact, substrate deformation, and anchoring of the first layer, and stage (2) with subsequent film growth and particle consolidation. The phenomena present during the deposition of ceramic particles by AD are similar to those occurring during LPCS. Hanft et al. [73] divided particles by the size and stage of agglomeration and described possible processes in AD (see Figure 21a). The ceramic particles size ready to bond is in the range of 200 nm-2 µm at intermediate energies. As the submicron particle strikes the substrate, cracks form by whole volume and fragmentation occurs due to impact pressure. Further moving or rotating of the fragments provides arrangement and densification. Upcoming particles cause rebinding of fragments, further plastic deformation and consolidation of the deposited material. The plasticity is described by quasi-static compression and respectively determined thresholds for plasticity [217]. Ceramic agglomerates impact the substrate and due to the kinetic energy get separated into fragments. The coating formation is possible, however the quality can be worsened. Large agglomerates will erode the substrate and rebound. The coating formation can be divided according to Figure 21b into stage (1), which concerns particles impact, substrate deformation, and anchoring of the first layer, and stage (2) with subsequent film growth and particle consolidation.
(a) (b) Figure 21. Possible particle-substrate interactions based on the speed and kinetic energy of the ceramic particles (a) and the room temperature impact consolidation process, with a distinction between stage 1 (anchor layer formation) and stage 2 (film buildup), during which particle hammering and fracturing takes place (b) [73].
The LPCS spraying process is performed at low temperatures, and thus there is an opportunity to use thermally sensitive materials without possible burning. To prepare ceramic powders with desired characteristics dedicated for LPCS (e.g., high purity ultrafine- Figure 21. Possible particle-substrate interactions based on the speed and kinetic energy of the ceramic particles (a) and the room temperature impact consolidation process, with a distinction between stage 1 (anchor layer formation) and stage 2 (film buildup), during which particle hammering and fracturing takes place (b) [73].
The LPCS spraying process is performed at low temperatures, and thus there is an opportunity to use thermally sensitive materials without possible burning. To prepare ceramic powders with desired characteristics dedicated for LPCS (e.g., high purity ultrafine-grained powders and nanopowders), the following wet-chemical methods can be used: wet ball milling, chemical co-precipitation, spray drying, or sol-gel. Wet ball milling performed in alcohol provides an efficient environment for homogenous mixing and enables a uniform distribution of components with additional satelliting [218]. As a result, wet-milled samples have a significantly smaller standard distribution compared to air milled [219]. Saghir et al. [220] ball-milled 5 µm sized plate-like alumina powder with various parameters in air and ethanol. Saghir et al. noticed that wet-milled powders underwent the greatest size reduction with a final average particle size of 0.29 µm and crystallite size of 10.13 nm (Figure 22), while Xu et al. [221] wet-milled ZnO varistor ceramics doped with Bi 2 O 3 , Sb 2 O 3 , Co 2 O 3 , Cr 2 O 3 , and MnO and achieved grain refinement. Turon-Vinas et al. [222] mixed in ball mill ceria-stabilized zirconia powders with 10 and 12 mol% ceria, containing 0.25 wt.% of Al 2 O 3 with different amounts of CaO in ethanol. Turon-Vinas et al. dried the powders, sieved (315 µm mesh), applied in cold isostatic pressing and proved increased mechanical properties of the material due to reduced grain size. The fine powder resulting from wet ball milling provides high density (above 99%) ceramic compacts in the sintering process [223]. grained powders and nanopowders), the following wet-chemical methods can be used: wet ball milling, chemical co-precipitation, spray drying, or sol-gel. Wet ball milling performed in alcohol provides an efficient environment for homogenous mixing and enables a uniform distribution of components with additional satelliting [218]. As a result, wetmilled samples have a significantly smaller standard distribution compared to air milled [219]. Saghir et al. [220] ball-milled 5 µm sized plate-like alumina powder with various parameters in air and ethanol. Saghir et al. noticed that wet-milled powders underwent the greatest size reduction with a final average particle size of 0.29 µm and crystallite size of 10.13 nm (Figure 22), while Xu et al. [221] wet-milled ZnO varistor ceramics doped with Bi2O3, Sb2O3, Co2O3, Cr2O3, and MnO and achieved grain refinement. Turon-Vinas et al. [222] mixed in ball mill ceria-stabilized zirconia powders with 10 and 12 mol% ceria, containing 0.25 wt.% of Al2O3 with different amounts of CaO in ethanol. Turon-Vinas et al. dried the powders, sieved (315 µm mesh), applied in cold isostatic pressing and proved increased mechanical properties of the material due to reduced grain size. The fine powder resulting from wet ball milling provides high density (above 99%) ceramic compacts in the sintering process [223]. Chemical co-precipitation is applied to homogeneous hydrolysis of various oxides. Many papers in the literature describe the production of nano-crystalline ceramic materials, e.g., ThO2 [224], cerium doped gadolinium gallium aluminium garnet with different Y-doping levels [225], low-agglomerated Yt-doped yttria-alumina garnet (YAG) ( Figure  23a) [226], Ce-doped YAG nanophosphors [227], and barium calcium zirconium titanate (BCZT) ((Ba0.85Ca0.15)(Zr0.1Ti0.9)O3) with a homogeneous particle size of approximately 500 nm (Figure 23b) [228]. Chemical co-precipitation is applied to homogeneous hydrolysis of various oxides. Many papers in the literature describe the production of nano-crystalline ceramic materials, e.g., ThO 2 [224], cerium doped gadolinium gallium aluminium garnet with different Y-doping levels [225], low-agglomerated Yt-doped yttria-alumina garnet (YAG) (Figure 23a) [226], Ce-doped YAG nanophosphors [227], and barium calcium zirconium titanate (BCZT) ((Ba 0.85 Ca 0.15 )(Zr 0.1 Ti 0.9 )O 3 ) with a homogeneous particle size of approximately 500 nm (Figure 23b) [228]. A method enabling control of agglomeration size of ceramic nanoparticles is spray drying. Powders prepared by spray drying have good flowability, narrow size distribution and controllable morphology. Produced in this way powder has granulation from tens of nanometres to hundreds of micrometres and depends mostly on the atomization nozzle type. However, it should be noted that the morphology of resultant particles depends not only on the size distribution of initial ceramics but also on agglomeration tendency in the suspension and mechanical strength of the shell of a granule provided by polymer additives during the drying process [229]. The influence of binder on the morphology was analysed by Kim and Jung [230], who concluded that the sphericity of Al2O3-ZrO2 particles is improved with increasing the viscosity of the solution. On the other hand, Wang et al. [231] produced hydroxyapatite (HA) microspheres and found that the particles had spherical morphology and smooth surface ( Figure 24), but did not have uniform size distributions. The mean size of the particles increased with slurry concentration and compressed air flow rate. Many studies have described the optimization of powders by spray drying for further application in thermal spraying. Bertrand et al. [232] prepared agglomerates of two oxide ceramics (Al2O3 and Y2O3-ZrO2) and shown that there is a qualitative relation between the sedimentation behaviour and the agglomerate shape (solid or hollow), while Vicent et al. [233] applied spray drying to produce free-flowing microsized nanostructured agglomerated TiO2 powder (P25 mixture of anatase and rutile) from nanosized particles with an average primary size of ~20 nm for atmospheric plasma spraying process. Chahal et al. [234] used the spray drying process to prepare calcium carbonate powder for thermal spray processes and obtained large, porous, hollow, and spherical particles ranging between 14 and 201 µm. However, in this case, the powder had to be sieved before the spraying process. To solve the problem of particle pores, density, and size, Bian et al. [134] prepared by spray drying a nanostructured mixture of Al2O3-13 wt.%TiO2 composite powders, and then heat and plasma treated. The pores in the particles were decreased after heat treatment, while plasma treatment increased the density and maintained a large number of nano-sized grains ( Figure 25). A method enabling control of agglomeration size of ceramic nanoparticles is spray drying. Powders prepared by spray drying have good flowability, narrow size distribution and controllable morphology. Produced in this way powder has granulation from tens of nanometres to hundreds of micrometres and depends mostly on the atomization nozzle type. However, it should be noted that the morphology of resultant particles depends not only on the size distribution of initial ceramics but also on agglomeration tendency in the suspension and mechanical strength of the shell of a granule provided by polymer additives during the drying process [229]. The influence of binder on the morphology was analysed by Kim and Jung [230], who concluded that the sphericity of Al 2 O 3 -ZrO 2 particles is improved with increasing the viscosity of the solution. On the other hand, Wang et al. [231] produced hydroxyapatite (HA) microspheres and found that the particles had spherical morphology and smooth surface ( Figure 24), but did not have uniform size distributions. The mean size of the particles increased with slurry concentration and compressed air flow rate. Many studies have described the optimization of powders by spray drying for further application in thermal spraying. Bertrand et al. [232] prepared agglomerates of two oxide ceramics (Al 2 O 3 and Y 2 O 3 -ZrO 2 ) and shown that there is a qualitative relation between the sedimentation behaviour and the agglomerate shape (solid or hollow), while Vicent et al. [233] applied spray drying to produce free-flowing micro-sized nanostructured agglomerated TiO 2 powder (P25 mixture of anatase and rutile) from nanosized particles with an average primary size of~20 nm for atmospheric plasma spraying process. Chahal et al. [234] used the spray drying process to prepare calcium carbonate powder for thermal spray processes and obtained large, porous, hollow, and spherical particles ranging between 14 and 201 µm. However, in this case, the powder had to be sieved before the spraying process. To solve the problem of particle pores, density, and size, Bian et al. [134] prepared by spray drying a nanostructured mixture of Al 2 O 3 -13 wt.%TiO 2 composite powders, and then heat and plasma treated. The pores in the particles were decreased after heat treatment, while plasma treatment increased the density and maintained a large number of nano-sized grains ( Figure 25). The sol-gel (SG) method offers unlimited possibilities for producing different materials at room temperature. It is essential for organic or biological modifications because it does not cause thermal degradation of materials [235]. There are alternative high-temperature approaches, such as the Pechini method [236] or the combustion method [237]. The SG technique also offers unique possibilities for generating materials with different shapes because the process is performed in the liquid medium. Matrices produced in this way can be porous or dense, depending on the final application. Porosity in a material is essential for potential applications, especially when active substances change their physicochemical properties (e.g., colour) in contact with extrinsic factors (gas and liquid) coated inside the matrix. Precursors offer numerous possibilities of modification of final products by adding functional groups. As a result, material properties can be changed, e.g., the affinity of metals, flexibility, or hydrophobicity [236,238,239]. It is worth emphasizing that the drying step, when water and other volatile liquids are removed, can be performed at room temperature. The resulting dry amorphous powder forms agglomerates consisting of the particles linked by electrostatic or van der Waals forces. However, uncontrolled room temperature drying and ageing remove organic liquids incompletely. The synthesis remains play a role of organic binder holding particles together and can be used in powders preparation suiting LPCS [240][241][242]. Considering the strength of the attractive force between particles, two types of agglomeration can be distinguished, namely soft and hard.
In non-sintered soft agglomerates weak liquid bridge forces hold the particles together, while in the case of sintered hard aggregates, particles are bound due to chemical The sol-gel (SG) method offers unlimited possibilities for producing different materials at room temperature. It is essential for organic or biological modifications because it does not cause thermal degradation of materials [235]. There are alternative high-temperature approaches, such as the Pechini method [236] or the combustion method [237]. The SG technique also offers unique possibilities for generating materials with different shapes because the process is performed in the liquid medium. Matrices produced in this way can be porous or dense, depending on the final application. Porosity in a material is essential for potential applications, especially when active substances change their physicochemical properties (e.g., colour) in contact with extrinsic factors (gas and liquid) coated inside the matrix. Precursors offer numerous possibilities of modification of final products by adding functional groups. As a result, material properties can be changed, e.g., the affinity of metals, flexibility, or hydrophobicity [236,238,239]. It is worth emphasizing that the drying step, when water and other volatile liquids are removed, can be performed at room temperature. The resulting dry amorphous powder forms agglomerates consisting of the particles linked by electrostatic or van der Waals forces. However, uncontrolled room temperature drying and ageing remove organic liquids incompletely. The synthesis remains play a role of organic binder holding particles together and can be used in powders preparation suiting LPCS [240][241][242]. Considering the strength of the attractive force between particles, two types of agglomeration can be distinguished, namely soft and hard.
In non-sintered soft agglomerates weak liquid bridge forces hold the particles together, while in the case of sintered hard aggregates, particles are bound due to chemical The sol-gel (SG) method offers unlimited possibilities for producing different materials at room temperature. It is essential for organic or biological modifications because it does not cause thermal degradation of materials [235]. There are alternative high-temperature approaches, such as the Pechini method [236] or the combustion method [237]. The SG technique also offers unique possibilities for generating materials with different shapes because the process is performed in the liquid medium. Matrices produced in this way can be porous or dense, depending on the final application. Porosity in a material is essential for potential applications, especially when active substances change their physicochemical properties (e.g., colour) in contact with extrinsic factors (gas and liquid) coated inside the matrix. Precursors offer numerous possibilities of modification of final products by adding functional groups. As a result, material properties can be changed, e.g., the affinity of metals, flexibility, or hydrophobicity [236,238,239]. It is worth emphasizing that the drying step, when water and other volatile liquids are removed, can be performed at room temperature. The resulting dry amorphous powder forms agglomerates consisting of the particles linked by electrostatic or van der Waals forces. However, uncontrolled room temperature drying and ageing remove organic liquids incompletely. The synthesis remains play a role of organic binder holding particles together and can be used in powders preparation suiting LPCS [240][241][242]. Considering the strength of the attractive force between particles, two types of agglomeration can be distinguished, namely soft and hard.
In non-sintered soft agglomerates weak liquid bridge forces hold the particles together, while in the case of sintered hard aggregates, particles are bound due to chemical diffusion. The hard agglomeration generates problems with breaking down during compaction, which results in incomplete densification of the particles [243]. This may be troublesome for LPCS needs agglomerated particles of a specific size to overcome the bow shock and form a coating.
In the literature, many reports concerning various ceramic materials produced via SG can be found, e.g., ZrO 2 -MgO nanocomposites [244], ultrafine alumina powders (<10 nm) [245], AlON powders by the nitritation of SG-derived alumina nanoparticles [246], nanoscale ZnTiO 3 powders [247]. In some papers, SG is paired with thermal spraying methods, of which plasma spraying is most recently applied. The SG enables various modifications of powder particle surfaces to increase the thickness of thermally sprayed coatings or enhance the adhesion force between the coating and substrate (Figure 26) [248]. However, due to nanosize combined with light weight and low density, the thermal spray coating process of nanopowders is characterized by poor flowability, leading to limited deposition and uneven coating thickness. In this case, SG can provide nano-sized powder (e.g., yttria stabilized zirconia (YSZ)) and bind its particles to microsized agglomerates by polyvinyl alcohol [249,250]. diffusion. The hard agglomeration generates problems with breaking down during compaction, which results in incomplete densification of the particles [243]. This may be troublesome for LPCS needs agglomerated particles of a specific size to overcome the bow shock and form a coating.
In the literature, many reports concerning various ceramic materials produced via SG can be found, e.g., ZrO2-MgO nanocomposites [244], ultrafine alumina powders (<10 nm) [245], AlON powders by the nitritation of SG-derived alumina nanoparticles [246], nanoscale ZnTiO3 powders [247]. In some papers, SG is paired with thermal spraying methods, of which plasma spraying is most recently applied. The SG enables various modifications of powder particle surfaces to increase the thickness of thermally sprayed coatings or enhance the adhesion force between the coating and substrate ( Figure 26) [248]. However, due to nanosize combined with light weight and low density, the thermal spray coating process of nanopowders is characterized by poor flowability, leading to limited deposition and uneven coating thickness. In this case, SG can provide nano-sized powder (e.g., yttria stabilized zirconia (YSZ)) and bind its particles to microsized agglomerates by polyvinyl alcohol [249,250]. Reprinted with permission from [248]. Copyright 2020 Elsevier.
Powders produced by SG can be dried in various temperatures to obtain various polymorphs, for instance, TiO2 amorphous powder can be produced by drying at room temperature, while anatase and rutile by drying the same powder at 500 and 800 °C, respectively. In my previous research, I produced nanosized TiO2 powder particles of spherical shape with sizes up to 500 nm [240,241,251]. The size of produced agglomerates was in the range of 3.6-78.6 µm (D 0.5 = 35.9 µm), 3.4-70.4 µm (D 0.5 = 19.4 µm), and 6.9-96.7 µm (D 0.5 = 35.9 µm), for amorphous phase, anatase, and rutile powder, respectively. The amorphous agglomerates seemed to be more porous compared to anatase or rutile (Figure Powders produced by SG can be dried in various temperatures to obtain various polymorphs, for instance, TiO 2 amorphous powder can be produced by drying at room temperature, while anatase and rutile by drying the same powder at 500 and 800 • C, respectively. In my previous research, I produced nanosized TiO 2 powder particles of spherical shape with sizes up to 500 nm [240,241,251]. The size of produced agglomerates was in the range of 3.6-78.6 µm (D 0.5 = 35.9 µm), 3.4-70.4 µm (D 0.5 = 19.4 µm), and 6.9-96.7 µm (D 0.5 = 35.9 µm), for amorphous phase, anatase, and rutile powder, respectively. The amorphous agglomerates seemed to be more porous compared to anatase or rutile ( Figure 27). The size of powders was appropriate for LPCS. What is more, proper modifications ensured particles surface functionalization, e.g., by providing fluorinated groups to obtain coatings with superhydrophobic properties in further work with LPCS ( Figure 28) [242]. The spraying conditions (e.g., low process temperature) minimize the heating of the powder in the working gas stream and preserve the functional material from burning or decomposition.  27). The size of powders was appropriate for LPCS. What is more, proper modifications ensured particles surface functionalization, e.g., by providing fluorinated groups to obtain coatings with superhydrophobic properties in further work with LPCS ( Figure 28) [242]. The spraying conditions (e.g., low process temperature) minimize the heating of the powder in the working gas stream and preserve the functional material from burning or decomposition.   [242].
The nanoparticles agglomeration can be improved by adding a binder. Yang et al. [252] deposited TiO2 coating with a mean thickness of 10-15 µm using anatase particles agglomerated by polyvinyl alcohol binder. Salim et al. [253] produced anatase powder by hydrolysis of TiOSO4 in distilled water with a small addition of inorganic salt (ammonium sulfate) working as a binder combined with hydrothermal post-treatment process and sprayed 150 µm thick TiO2 coating. Salim et al. claimed that NH4 + and SO4 2− ions adsorbed on the surface of TiO2 and post hydrothermal post-treatment favour agglomerated particles break down on impact onto the substrate due to the induced nanoporosity and were the key factor to a build-up of the coating. Further analysis performed by Toibah et al. [254] showed that adding the (NH4)2SO4 binder enhanced the agglomeration process of TiO2 and promoted mobility of dislocation during the CS process. It should be emphasised that soft agglomerates provide higher quality coating compared to sintered aggregates, which are difficult to fracture upon impact [73,255,256].

LPCS Ceramic Coatings Applications
Ceramic nanostructured coatings are a fundamental material of many functional applications, such as self-cleaning and antifouling surfaces [257], implants and biocompatibility [258], biomedical devices [259], tools [260], solar cells, Li-ion batteries, and solid oxides fuel cells [261]. Particular attention is paid to the nano-porous structures, which merit is extremely large surface area and other specific properties in comparison to bulk material [262]. Kinetics processes enhance ceramic particle's breaking into small fragments within coatings with defined density. As a result, some local porosity can be formed in the coatings [240,241]. What is more, due to high-velocity impact, impact-induced fragmentation and compression in LPCS, nanoparticles ceramic particles can provide coatings with various thicknesses [263]. In contrast to the AD method, LPCS work in atmospheric conditions and a shock wave is formed above the substrate. Therefore, agglomerated particles are needed in LPCS to enhance DE. The nanoparticles agglomeration can be improved by adding a binder. Yang et al. [252] deposited TiO 2 coating with a mean thickness of 10-15 µm using anatase particles agglomerated by polyvinyl alcohol binder. Salim et al. [253] produced anatase powder by hydrolysis of TiOSO 4 in distilled water with a small addition of inorganic salt (ammonium sulfate) working as a binder combined with hydrothermal post-treatment process and sprayed 150 µm thick TiO 2 coating. Salim et al. claimed that NH 4 + and SO 4 2− ions adsorbed on the surface of TiO 2 and post hydrothermal post-treatment favour agglomerated particles break down on impact onto the substrate due to the induced nanoporosity and were the key factor to a build-up of the coating. Further analysis performed by Toibah et al. [254] showed that adding the (NH 4 ) 2 SO 4 binder enhanced the agglomeration process of TiO 2 and promoted mobility of dislocation during the CS process. It should be emphasised that soft agglomerates provide higher quality coating compared to sintered aggregates, which are difficult to fracture upon impact [73,255,256].

LPCS Ceramic Coatings Applications
Ceramic nanostructured coatings are a fundamental material of many functional applications, such as self-cleaning and antifouling surfaces [257], implants and biocompatibility [258], biomedical devices [259], tools [260], solar cells, Li-ion batteries, and solid oxides fuel cells [261]. Particular attention is paid to the nano-porous structures, which merit is extremely large surface area and other specific properties in comparison to bulk material [262]. Kinetics processes enhance ceramic particle's breaking into small fragments within coatings with defined density. As a result, some local porosity can be formed in the coatings [240,241]. What is more, due to high-velocity impact, impact-induced fragmentation and compression in LPCS, nanoparticles ceramic particles can provide coatings with various thicknesses [263]. In contrast to the AD method, LPCS work in atmospheric conditions and a shock wave is formed above the substrate. Therefore, agglomerated particles are needed in LPCS to enhance DE.
Deposition of ceramic particles requires specific parameters. High pressure above 2 MPa enables anchoring of the ceramic particles in a plastic substrate, however, incoming particles cause blasting effects resulting in defects and thin thickness of the coating [73,254]. Deposition of ceramics by LPCS is conditioned significantly by powder preparation method [240,241]. Amorphous agglomerated particles manufactured by the SG method and dried at room temperature showed high porosity and residue of organic binder, composed mostly of alcohol, which enabled compaction of the submicron powder particles. Application of high working gas temperature of 400 • C in LPCS resulted in crack-free and thick coating formation with amorphous TiO 2 to the anatase phase transition. According to the literature [263][264][265][266][267][268] amorphous oxides, known as soft ceramics, are exhibiting remarkable plastic deformation at moderate temperatures.
CS, as a dynamic process, generates enormous amounts of kinetic energy, which is transformed into plastic deformation and enables phase transition. Therefore, controlled transitions of amorphous to crystalline phase are possible ( Figure 29). The phase transition of amorphous material can be controlled by the volume fraction of the crystalline phase, which prevents propagation of the cracks and supports the formation of multiple shear bands [269,270]. Moreover, the deformation of amorphous ceramic can be influenced by the coexistence of the amorphous phases and crystalline phases [269][270][271][272]. Xu et al. [272] analysed amorphous ceramics in hot pressing and concluded that amorphous ceramic, as a metastable material, shows large atomic mobility and local free volume, enabling the formation of shear bands and further plastic deformation. Therefore, the mechanism responsible for ceramic deposition is based on (i) slipping or sliding of fine particles over particles and (ii) plastic deformation resulting from the amorphous state with larger atomic mobility and local free volume, which is beneficial to the formation of shear bands. method and dried at room temperature showed high porosity and residue of organic binder, composed mostly of alcohol, which enabled compaction of the submicron powder particles. Application of high working gas temperature of 400 ˚C in LPCS resulted in crack-free and thick coating formation with amorphous TiO2 to the anatase phase transition. According to the literature [263][264][265][266][267][268] amorphous oxides, known as soft ceramics, are exhibiting remarkable plastic deformation at moderate temperatures.
CS, as a dynamic process, generates enormous amounts of kinetic energy, which is transformed into plastic deformation and enables phase transition. Therefore, controlled transitions of amorphous to crystalline phase are possible ( Figure 29). The phase transition of amorphous material can be controlled by the volume fraction of the crystalline phase, which prevents propagation of the cracks and supports the formation of multiple shear bands [269,270]. Moreover, the deformation of amorphous ceramic can be influenced by the coexistence of the amorphous phases and crystalline phases [269][270][271][272]. Xu et al. [272] analysed amorphous ceramics in hot pressing and concluded that amorphous ceramic, as a metastable material, shows large atomic mobility and local free volume, enabling the formation of shear bands and further plastic deformation. Therefore, the mechanism responsible for ceramic deposition is based on (i) slipping or sliding of fine particles over particles and (ii) plastic deformation resulting from the amorphous state with larger atomic mobility and local free volume, which is beneficial to the formation of shear bands.
It is worth emphasising that the mechanical properties of coatings strongly depend on the type of feedstock powder and the substrate preparation method as well. The amorphous powder with an organic binder enables the deposition of a coherent coating without structural defect [240,241]. According to my previous results [251], the adhesion measured by a scratch test of anatase LPCS coating sprayed of amorphous titania powder dried at room temperature was highest among other analysed coatings. The critical load of 15.8 N was achieved ( Figure 30). The result was comparable to the adhesion of suspension plasma sprayed rutile coating, which showed a critical load of 16.56 N [273]. Unfortunately, coating sprayed of anatase powder showed many defects (e.g., lamellar microcracks) which resulted mainly from differences in the thermal expansion coefficient of the metallic substrate and ceramic coating. Similar problems with microcracks and delamination of anatase coatings on steel substrate were noticed by Yamada et al. [274] when using nitrogen as a working gas. The coating quality was improved by applying helium.
(a) (b) Figure 29. XRD (a) and Raman (b) spectra obtained for coating deposited of amorphous powder with the use of air preheated to 600 °C. Reprinted with permission from [240]. Copyright 2019 Elsevier. Figure 29. XRD (a) and Raman (b) spectra obtained for coating deposited of amorphous powder with the use of air preheated to 600 • C. Reprinted with permission from [240]. Copyright 2019 Elsevier.
It is worth emphasising that the mechanical properties of coatings strongly depend on the type of feedstock powder and the substrate preparation method as well. The amorphous powder with an organic binder enables the deposition of a coherent coating without structural defect [240,241]. According to my previous results [251], the adhesion measured by a scratch test of anatase LPCS coating sprayed of amorphous titania powder dried at room temperature was highest among other analysed coatings. The critical load of 15.8 N was achieved ( Figure 30). The result was comparable to the adhesion of suspension plasma sprayed rutile coating, which showed a critical load of 16.56 N [273]. Unfortunately, coating sprayed of anatase powder showed many defects (e.g., lamellar microcracks) which resulted mainly from differences in the thermal expansion coefficient of the metallic substrate and ceramic coating. Similar problems with microcracks and delamination of anatase coatings on steel substrate were noticed by Yamada et al. [274] when using nitrogen as a working gas. The coating quality was improved by applying helium. Due to coatings purity, controlled phase and porosity, high adhesion and cohesion, LPCS can be applied to spray many ceramic materials. The TiO2 coating deposited on a metallic substrate improves surface properties, such as self-cleaning, anti-corrosive, or photocatalytic activity. Great potential in the processes of photocatalytic decomposition of organic pollutants gives amorphous titanium dioxide [275][276][277][278] and mixtures of crystalline polymorphs with amorphous TiO2 [279,280]. It arises from specific amorphous material properties, which favours the photocatalysis process: (i) the oxygen vacancies and defect states can promote the generation of photo-induced holes and hinder the recombination of electron-hole pairs and (ii) a high specific surface area and a large number of surface reaction sites of amorphous form make the reactive surface larger than in the case of anatase [281,282]. It should be noted that the long-term operation of anatase-amorphous coatings on the aluminium substrate in a high humidity environment affects its photocatalytic activity by the amorphous transition to the anatase-brookite mixture [283]. The crystallization of brookite was activated by two factors interacting at the same time namely oxygen defects of amorphous TiO2 and the effect of moisture on this specific system. The degradation efficiency of methylene blue after 4 h of UV irradiation by anataseamorphous and anatase-brookite coatings was 22% and 34%, respectively [283]. Zhou et al. [284] deposited by the LPCS process an agglomerated gallium nitride (GaN) nano-porous, thin coating (up to 10.4 µm) on stainless steel and achieved photocatalytic activities of about 33%. The obtained result was 9% higher compared to the powder and arose from the higher specific surface area and roughness that the coatings exhibit after the breakage of the particles during the cold spray. It is worth emphasizing that LPCS can be used to spray TiO2 onto thermally sensitive materials, such as polymers, providing new opportunities for coupled materials [285]. Fan et al. [286] sprayed nanocrystalline TiO2 by the vacuum AD process and obtained a similar coating consisting of agglomerated particles with a thickness of several hundred nanometers and a mesoporous microstructure for applications as photocatalytic degradation and dye-sensitized solar cells.
Ceramic coatings can be also applied successfully for biomedical applications [287][288][289]. Hydroxyapatite (HA) compared to titanium shows high bioactivity due to increased osseointegration capacities and similar chemical composition of the bone [290]. LPCS can restrain temperature drawbacks present in plasma spraying of HA, such as evaporation, phase alteration, residual stress, deboning or gas release [291]. Vilardell et al. [292] worked on Ti6Al4V substrate preparation to successfully spray hydroxyapatite (HA). The best quality and DE showed HA coatings deposited by LPCS onto a very rough and porous HPCS Ti bond coat. The HA particles impact the bond coat surface and anchor properly Due to coatings purity, controlled phase and porosity, high adhesion and cohesion, LPCS can be applied to spray many ceramic materials. The TiO 2 coating deposited on a metallic substrate improves surface properties, such as self-cleaning, anti-corrosive, or photocatalytic activity. Great potential in the processes of photocatalytic decomposition of organic pollutants gives amorphous titanium dioxide [275][276][277][278] and mixtures of crystalline polymorphs with amorphous TiO 2 [279,280]. It arises from specific amorphous material properties, which favours the photocatalysis process: (i) the oxygen vacancies and defect states can promote the generation of photo-induced holes and hinder the recombination of electron-hole pairs and (ii) a high specific surface area and a large number of surface reaction sites of amorphous form make the reactive surface larger than in the case of anatase [281,282]. It should be noted that the long-term operation of anatase-amorphous coatings on the aluminium substrate in a high humidity environment affects its photocatalytic activity by the amorphous transition to the anatase-brookite mixture [283]. The crystallization of brookite was activated by two factors interacting at the same time namely oxygen defects of amorphous TiO 2 and the effect of moisture on this specific system. The degradation efficiency of methylene blue after 4 h of UV irradiation by anatase-amorphous and anatase-brookite coatings was 22% and 34%, respectively [283]. Zhou et al. [284] deposited by the LPCS process an agglomerated gallium nitride (GaN) nano-porous, thin coating (up to 10.4 µm) on stainless steel and achieved photocatalytic activities of about 33%. The obtained result was 9% higher compared to the powder and arose from the higher specific surface area and roughness that the coatings exhibit after the breakage of the particles during the cold spray. It is worth emphasizing that LPCS can be used to spray TiO 2 onto thermally sensitive materials, such as polymers, providing new opportunities for coupled materials [285]. Fan et al. [286] sprayed nanocrystalline TiO 2 by the vacuum AD process and obtained a similar coating consisting of agglomerated particles with a thickness of several hundred nanometers and a mesoporous microstructure for applications as photocatalytic degradation and dye-sensitized solar cells.
Ceramic coatings can be also applied successfully for biomedical applications [287][288][289]. Hydroxyapatite (HA) compared to titanium shows high bioactivity due to increased osseointegration capacities and similar chemical composition of the bone [290]. LPCS can restrain temperature drawbacks present in plasma spraying of HA, such as evaporation, phase alteration, residual stress, deboning or gas release [291]. Vilardell et al. [292] worked on Ti6Al4V substrate preparation to successfully spray hydroxyapatite (HA). The best quality and DE showed HA coatings deposited by LPCS onto a very rough and porous HPCS Ti bond coat. The HA particles impact the bond coat surface and anchor properly by filling up the valleys of the surface roughness. According to the dilatometry graph, two different thermal treatments were performed at 1000 and 1400 • C to densify the coating structure ( Figure 31). Apart from substrate surface roughness, there are other process parameters, such as standoff distance, substrate heating temperature, and the number of sprays, which influences the HA coating properties. Moreover, despite the ideal bioactive compatibility of HA, low mechanical strength limits its use in loaded implants. Therefore Hasniyati et al. [293] used the design of experiment and analysed the effects of input LPCS process parameters on the thickness, nanohardness, and elastic modulus of the HA coating deposited on pure Mg. by filling up the valleys of the surface roughness. According to the dilatometry graph, two different thermal treatments were performed at 1000 and 1400 °C to densify the coating structure ( Figure 31). Apart from substrate surface roughness, there are other process parameters, such as standoff distance, substrate heating temperature, and the number of sprays, which influences the HA coating properties. Moreover, despite the ideal bioactive compatibility of HA, low mechanical strength limits its use in loaded implants. Therefore Hasniyati et al. [293] used the design of experiment and analysed the effects of input LPCS process parameters on the thickness, nanohardness, and elastic modulus of the HA coating deposited on pure Mg. The optimized HA coating was 49.77 µm thick, with nanohardness and elastic modulus of 462.61 MPa and 45.69 GPa, respectively.
(C) The particles agglomeration was used to spray other types of ceramic materials by LPCS, such as WO3, SiC, SiO2. Tungsten trioxide is mostly applied for: (i) hydrogen detection, (ii) fuel cell electrodes, (iii) photoanodes in photoelectrochemical cells for water splitting, pollutants degradation, air purification, and as an antimicrobial agent [294]. To The particles agglomeration was used to spray other types of ceramic materials by LPCS, such as WO 3 , SiC, SiO 2 . Tungsten trioxide is mostly applied for: (i) hydrogen detection, (ii) fuel cell electrodes, (iii) photoanodes in photoelectrochemical cells for water splitting, pollutants degradation, air purification, and as an antimicrobial agent [294]. To produce WO 3 coatings, Lee et al. [295] sprayed aggregated particles of 30-50 µm size, which were shattered and fractured upon impact on the substrate. Formed coatings had a thickness of up to 2 µm and consisted of very fine secondary particles, which provided good adherence and void reduction in the coating. In another study, Lee et al. tested WO 3 and Y 2 O 3 LPCS coating and noticed, that particles closest to the substrate were finer and better packed due to fragmentation of impacting agglomerates ( Figure 32) [296]. The SiC is applied for anti-oxidation at elevated temperatures due to thermophysical properties and the possibility of formation of a thin amorphous SiO 2 with appropriate fluidity and low oxidation diffusion coefficient as well [297]. Seo et al. [298] sprayed a rough and porous SiC powder with a mean size of 17 µm powder, which was crushed due to impact into nanometre-sized particles and anchored in Inconel 625 substrate. The anti-oxidation of the metallic substrate was three times higher compared to the uncoated substrate. What is more, a significant effect on the Inconel 625 protection from oxygen diffusion played SiO 2 thin film formed beneath SiC. The silica coating is an attractive material for hydrophobic [299] or hydrophilic [300] applications, depending on material functionalization. Therefore, combining various techniques (e.g., SG method for powder material production and LPCS for coating deposition) enables functionalization of the substrate surface. The SG synthesis allows full control of produced oxide materials with provided deformability due to amorphous form. Submicron silica particles covered with C 14 H 19 F 13 O 3 Si shell support multilevel roughness of coating and enhance the coating hydrophobicity [242]. The surface of as-sprayed SiO 2 coatings modified with 0.15 mL C 14 H 19 F 13 O 3 Si gave the highest contact angle (CA) of 153.7 • . The coating maintains its superhydrophobic properties in severe conditions, which confirmed durability tests consisting of: (i) sliding sample surface on the surface of 800-grit sandpaper (Figure 33a), (ii) two-hours annealing at different temperatures varying from 50 to 500 • C and quenching in the air in (Figure 33b), (iii) immersion in water and absolute alcohol (Figure 33c), and (iv) ultrasonic bath in absolute alcohol (Figure 33d). It was concluded that merely hightemperature treatment can significantly reduce hydrophobic properties by decomposition of the functionalizing precursor, C 14 H 19 F 13 O 3 Si. Table 4 shows the main applications of ceramic coatings produced by LPCS. Table 4. Selected applications of the LPCS ceramic coatings.

Future Perspectives
The combination of the CS process with the appropriate powder preparation method opens new possibilities in surface engineering. The fabrication of nanostructured functional CS coatings is promising in many non-traditional fields, e.g., photocatalysis [283,284], dyesensitized solar cell [301,302], electro-ceramic for piezoelectric devices and electro-optic materials for optical devices [50,303] solid oxide fuel cells [304][305][306], bioactivity [307][308][309][310]. The spraying process is increasingly operator-friendly, as troublesome technical aspects are being eliminated, e.g., nozzle clogging is solved by water cooling system, fine agglomerating particles are fed by aerosol powder feeders, the powder particles velocity is easily increased in the newest units by increased parameter ranges, the gas pressure up to 10 MPa, and the gas temperature up to 1100 • C. It should be noted that there are applications in which technologically more advanced HPCS can be replaced by LPCS. For example, ceramic deposition is processed with low working gas pressure. On the other hand, HPCS increase the plastic deformation of metal particles in metal-ceramic mixtures and, as a result, increase DE and coating compactness as well. Therefore, the increased range of spraying parameters in newly produced cold spray units, especially working gas pressures, seems to be sensible in the case of MMC coatings deposition. However, in this solution, the gas consumption extremally increases process costs. As described above various CS coatings indicate that the basic process limitation has been overcome, as high content MMC composite and pure ceramic coatings are being sprayed extending significantly process applications. Further CS experiments should be concentrated on the following challenges: (i) selecting optimal parameters for powder preparation to CS; (ii) applying of ceramic or metal-ceramic powder material modifications or CS process optimization, e.g., new nozzle design, to spray highly coherent coatings without vacuum or further PSHT; (iii) balancing work hardening with toughness and ductility of MMC coating by CS parameters adjustment mainly for additive manufacturing applications; (iv) tailoring the ratio, size, concentration, and distribution of ceramic phase in the deposited MMC coating; (v) analyzing nonmetallic substrates preparation method, e.g., surface texturing, for improved bonding; (vi) selecting parameters to control the phase transition, e.g., amorphous to anatase in the spraying process or intermetallic formation in PSHT.

Conclusions
CS is one of the most intensively developed techniques among thermal spraying methods. The benefits of CS arising from the utilization of high kinetic energy instead of thermal energy makes it a perfect technology for the deposition of various materials. Due to the considerably higher DE of HPCS, for many years LPCS was considered only a budget version of CS. Nevertheless, the latest research results showed significant progress and new possibilities of the LPCS. The DE in LPCS is usually improved by mixing soft metal powder with hard phase (e.g., ceramic powder), which provides a tamping effect and increases plastic deformation. Furthermore, to increase DE without additional processes (e.g., oxide reduction), LPCS parameters should be optimized, such as: (i) particle size, (ii) working gas, as well as (iii) nozzle length and expansion ratio.
A basic method to deposit ceramic particles by LCPS is the application of PRMMC with a controlled admixture of metal powder to work as a binder. Kinetic spraying provides many merits, such as: lack of tensile thermal stresses, uncontrolled phase transformation, decarburization, oxidation, or high porosity. The mixture of ductile matrix and hard reinforcement phase result in combined properties of the PRMMC LPCS coatings. The powders mixture can be prepared by: (i) mechanical blending of powders, (ii) satelliting, (iii) powder cladding, (iv) mechanical ball milling, (v) ball milling combined with SHS, and (vi) spray drying. Each method has its advantages and disadvantages. Mechanical blending is a common technique. However, it has some limitations, e.g., different sizes of particles, morphology, or density, which result in various ranges of particles velocities and thus divergence in DE and nonuniform ceramic and metal distribution. By spray drying, powder agglomerates can be produced, increasing coating uniformity. A high and controlled volume fraction of the hard phase can be provided by powder cladding. Ball milling ensures composites with well-dispersed nano-sized particles. Nevertheless, due to enhanced work hardening of the ductile phase, the DE of the mixture in LPCS can be decreased. A proper powder preparation increases the ceramic content in the coatings. However, despite the dominating contribution of ceramic powder in the mixture, a significant part will rebound, decreasing the ceramic DE. The bonding mechanism of ceramic in PRMMC LPCS coatings is based on the plastic deformation of metallic particles at a high strain rate. The impacting metal particles show the highest shear strain at the particle's interface. Nevertheless, metal-ceramic LPCS coatings show advanced functionality and include many applications.
Deposition of pure ceramic powder by LPCS is more complicated as the material is brittle. The mechanism with plastic and features of inelastic deformation may occur for ceramics. However, fine particles have to be applied in the deposition process. In LPCS, the stream of particles has to overcome the air atmosphere, which decelerates the particles. Therefore, increased working gas velocity should be used. As a result, a bow shock forms above the substrate and ejects fine particles from the stream. There are several requirements for powder preparation to spray ceramic particles by LPCS: (i) nanosized particles should be agglomerated to overcome bow shock, (ii) the agglomerates should be porous to fracture and (iii) have structures with a continuous epitaxial-like crystal array. Due to high-velocity impact, impact-induced fragmentation, and compression in LPCS, nanoparticles ceramic particles can provide coatings with various thicknesses.
The preparation of agglomerated ceramic powders with advisable characteristics dedicated for LPCS can be performed by several wet-chemical methods: wet ball milling, chemical co-precipitation, spray drying, or sol-gel. Due to wet condition powders having a significantly smaller standard distribution of particles and controllable morphology compared to air milled, the SG method offers additionally unlimited possibilities of producing different materials at room temperature with controlled porosity. The resulting dry amorphous powder forms agglomerates consisting of the particles linked by electrostatic or van der Waals forces. Such soft agglomerates provide higher quality LPCS coating compared to sintered aggregates, which are difficult to fracture upon impact. The amorphous oxides are exhibiting remarkable plastic deformation at moderate temperatures, and due to enormous kinetic energy in the LPCS process, controlled phase transition into crystalline phase can be initiated. Therefore, the mechanism responsible for ceramic deposition is based on the following steps: (i) slipping or sliding of fine particles over particles and (ii) plastic deformation resulting from the amorphous state with larger atomic mobility and local free volume, which is beneficial to the formation of shear bands.
The deposition of pure ceramic coatings opens new applications for LPCS. However, much more work is needed to explore new horizons and further possibilities of the CS method.