Evaluation of the Multi-Structural Potential of Ni-Co/SiC Nanocomposite Coatings Electrodeposited in API 5L X80 Steel

The use of nanocomposite coatings on carbon steel has been very promising. In this paper, the formation mechanism of multilayer of Ni-Co/SiC nanocomposite coating electrodeposited in API 5L X80 steel was investigated. The coatings were obtained by galvanostatic deposition technique using a single bath and a single cathodic current density value. The results showed a variation in morphology and chemical composition of the coatings both on the surface and along the cross-section at all time conditions tested, confirming the functional gradient of the coating. The formation of the Ni-Co/SiC nanocomposite coating occurred through the multilayer deposition mechanism, with compositions mostly alternated between Ni and Co. The preferred orientation of the plane (220) and phase structure FCC remained constant on the surface of all the obtained samples. It was observed that the coating became more compact in the region located closer to the substrate, where an increase in micro-hardness was observed.


Introduction
During the last few decades, nanocomposite coatings became widely used in many strategic areas in the industry due to its unique mechanical properties, self-lubricity, thermal stability, oxidation, corrosion and wear resistance 1,2 . So far, many techniques have been employed to produce nanocomposite coatings, including: powder metallurgy, foil diffusion bonding, stir casting, spray deposition, physical vapor deposition, as well as electrolytic deposition 3,4 . Electrodeposition is relatively simple to control, efficient, low initial capital investment and high quality, when compared to other techniques 5,6 .
The obtention of Ni-Co/SiC nanocomposite coatings by electrodeposition comes from the addition of SiC nanoparticles to an electrolytic bath composed of Ni and Co salts 7 . The incorporation of nanoparticulate SiC, which has high micro-hardness, good stability and resistance to wear and corrosion at high temperatures, to the Ni-Co metal matrix can provide unique properties to Ni-Co/SiC coatings 8,9 . This inclusion provides a diversity of applications of Ni-Co-based composite coatings in the automotive, aerospace, automotive, petrochemical and other industries due to its good adhesion to the substrate, low residual stress, low porosity, high hardness, anti-wear and anti-corrosion properties 1,4,10 .
The electrodeposition of Ni-Co matrix coatings is governed by the anomalous co-deposition of Ni 2+ and Co 2+ ions, whose reduction in the cathode generates intermediate species that alter the bath composition, the coating surface and the incorporation of nanoparticles 6,9 . The variation of process parameters such as current density, stirring rate, and composition in the bath causes changes and can influence the system producing multi-structured coatings with a functional gradient, consisting of multiple layers with different compositions 5,11,12 . Studies in the area of multistructured coatings have been carried out to improve the performance of the coating, which leads to a wide variety of applications. Functionally graded composite coatings constitute a class of materials whose surface and interface properties can function efficiently due to the gradual variation of the particle content with the coating thickness in order to satisfy specific needs 4,11,13 .
The growing interest in research on Ni-Co/SiC nanocomposite coatings shows that it is possible to obtain these electrodeposits on several metallic surfaces, such as copper, aluminum, sintered NdFeB material and mild steel, for example 1,8,[14][15][16] . Despite these possibilities, few studies have been focused on obtaining nanocomposite coating in carbon steel wich is a very important material in the industry and requires protection. The Ni-Co / SiC nanocomposite coating was the subject of a previous study 16 that showed excellent corrosion resistance and hardness properties when applied to API 5L X80 steel, a material used in pipelines in the oil industry. Yang and Cheng 4 studied the application of the coating against erosion-enhanced corrosion of carbon steel pipes in oilsand slurry. Lari Baghal, Heydarzadeh Sohi and Amadeh 15 tested the application of this coating on aluminum pistons for engine, utilized under fairly high temperature and wearing conditions, and found promising results. Furthermore, it is important that electrodeposition is studied on several substrates due to the influence of hydrogen production reaction 17,18 .
Most studies about this theme are focused on a singlelayer Ni-Co/SiC nanocomposite coatings obtained by electrodeposition. However, there has never been any study conducted to examine the potential of multi-structural coating on any substrate, much less in carbon steel. Moreover, not enough emphasis has been put on studying the crosssectional areas and their characteristics such as morphology, composition, and properties such as micro-hardness. This study is made relevant because it aims to explore the possibility of obtaining a multi-structured coating of Ni-Co/SiC, in a steel substrate, and to provide information to clarify the process of formation of multiple layers. Additionally, this work intends to investigate the formation mechanism of multilayer of Ni-Co/SiC nanocomposite coating electrodeposited in API 5L X80 steel. The coatings were obtained by galvanostatic deposition technique using a single bath and a single cathodic current density value. Morphology, chemical composition and micro-hardness of the surface and the cross-section of the coatings were studied and related to multi-structural potential of samples.

Substrate preparation
API 5L X80 steel pipeline was cut into 15 mm x 10 mm x 6 mm specimens with this chemical composition (%): C 0.030, S 0.004, Cr 0.159, Mn 1.72, Si 0.170, Al 0.028 and residual Fe. All specimens had their sides sealed with epoxy resin, and a rectangular work area of 1.5 cm 2 was left and prepared to receive the coatings. Before electroplating, the working face was ground sequentially with 220, 320, 400 and 600 grit emery papers and polished with a 1 µm Al 2 O 3 powder suspension 4 . Then, the specimens were cleaned in an electrolyte containing 30 g/L Na 2 CO 3 and 10 g/L NaOH at room temperature (~ 25 ºC), and activated in 1:1 (v/v) HCl solution for 20 s 19 .

Electrolyte and electrodepositing parameters
The electrolytic bath compositions and plating parameters used in electrodepositions are shown in Table 1. SiC nanoparticles (50 -60 nm) were obtained from IoLi.Tec Ionic Liquids Technologies GmbH ® and used as received with any modification. All the chemicals used in the experiment were analytical reagent and deionized water as solvent. The electrolyte bath was stirred magnetically with 600 rpm for 24 hours beforehand and was done during the plating in order to achieve a homogeneous dispersion and full suspension of nanoparticles during electrodeposition 20 .
In ordem to investigate the deposition of multilayers and the formation mechanism of the coating nanocomposite Ni-Co/SiC, the following deposition times were used: 10, 20, 30, 40, 50 and 60 min. The coatings were obtained by galvanostatic deposition technique using a single bath and a single cathodic current density value (5.5 A dm -2 ). The cathodic current density value was defined by a previous study and corresponded to the current condition, wich was able to obtain the coating with the best properties for this system 16 . The bath pH was maintained at 4.5, it was adjusted with NH 4 OH or H 2 SO 4 when necessary 7 . The temperature of the electrolytic bath and stirring rate were maintained at 55 °C and 600 rpm, respectively. Electrodeposition was performed using a conventional electrochemical cell made of Pyrex® glass that contained an electrolytic bath, in which the steel specimen was inserted as a cathode and the platinum electrode as an inert anode, at a distance of 3 cm from each other. Each sample was obtained in a bath and used only once, so as to ensure the same conditions as in Table 1 for all coatings. The current control was performed by an AUTOLAB® Galvanostat/Potentiostat, controlled by the Nova 1.11 Program. All the obtained samples were washed by ultrasonic stirring for about 8 min to remove any weakly adsorbed SiC nanoparticles.

SEM and EDS characterization
The morphology and the chemical composition on the surface and cross-section of deposits were analyzed using a model Tescan ® Mira 3 Scanning Electron Microscopy coupled with Energy Dispersive Spectroscopy (SEM-EDS). For the analysis of the coating profile, each sample was embedded, so its cross-section was subjected to metallographic preparation. The chemical composition was examined in cross-section at depths of 10 µm, 20 µm and 30 µm, as it was measured in relation to the coating surface level. The thickness of the deposits was determined by the arithmetic average of 5 measurements 21 . With a view to understand the mechanism of coating formation, the cross-sectional samples were etched in a solution of nitric acid (HNO 3 ) and acetic acid (CH 3 COOH) (1: 1) for 5 s 22 .

XRD characterization
X-Ray Diffraction measurements were carried out by using a Shimadzu ® XRD-7000 diffractometer employing Cu Kα radiation of wavelength 0.154 nm. The scan rate was 0.05º per second over a 2θ ranging from 20º to 100º 23 . Crystalline structure, texture coefficient (TC) and grain size were determined on the surface of the deposits 24 .

Micro-hardness measurement
The Vickers micro-hardness was measured on the surface and cross-section of the coatings using a Vickers diamond indenter. On the surface, the applied load was 200 g for 15 s and in the cross-section it was 10 g for 15 s 19 . This decrease in load made it possible to determine the micro-hardness at various points in the cross-section and, thus, to establish its variation along the thickness. Ten measurements were conducted on each sample to obtain the average value 25 . Each profile was performed in a diagonal line with reference to the surface of the coating, from where the indentations started. Figures 1 and 2 show, respectively, the surface morphology and chemical composition of Ni-Co/SiC nanocomposite coatings obtained by galvanostatic deposition within 10, 20, 30, 40, 50 and 60 min. Figure 3 shows the XRD spectrum of the sample surface obtained in a deposition time of 10 min and 20 min, and Table 2 shows the texture coefficient (TC) and grain size calculated from the diffractograms, based on the plane (220).

Surface characterization
In Figure 1, it can be seen that the substrate surface was coated in all samples. The morphology observed in Figure 1 and the chemical composition of the coating shown in Figure 2 varied considerably depending on the deposition time of the electrolyte components. In Figure 1-A, it can be seen that the coating obtained within 10 min presented a branched, acicular structure (needle-like), typical of cobalt and richcobalt solid solutions as shown in Figure 2. Moreover, it presented the highest grain size value (96,37 nm) among all samples ( Table 2). The deposit formed after 10 min represents a high porosity layer, due to the empty spaces between the cobalt needle-like structures. These void spaces are partially filled with globular formations which are attributed to the deposition of SiC particles entrapped by nickel. Figure 1B shows the presence of "cauliflower" structures attributed to nickel-rich coatings, indicating that on this surface, the noblest element (nickel) is in greater concentration despite the occurrence of anomalous codeposition in Ni-Co matrix coatings 9 . The surface of the coating obtained after   Figure 1B) showed a morphology that was completely different from the coating obtained within 10 min ( Figure 1A). In this sense, it had a significant reduction in the grain size that reached the lowest value among the analyzed samples. , about 38.97 nm ( Table 2). This 59% reduction in grain size in relation to the 10 min sample is due to the distinct characteristics between the surfaces of the coatings formed after 10 min and 20 min. This result is supported by the chemical composition ( Figure 2) of the sample obtained after 20 min, which presented the highest nickel (59 wt.%) and SiC (6.2 wt.%) contents, when compared to all the investigated samples. This indicates that nickel, whose deposition occurred among the spaces of cobalt needle-like structures, filled the spaces forming a new surface with a different morphology. According to Rudnik and Syrek, cobalt deposition provides surface roughness for nickel deposition and SiC trapping 23 . The presence of nickel in the coating structure tends to work by reducing the void spaces among the cobalt structures and, consequently, reducing the grain size 4 .
With 30 min of deposition time ( Figure 1C), the surface of the coating again presented, once more, structures in the   form of typical cobalt needle-like. However, the dimensions were smaller than the structures of the sample obtained within 10 min ( Figure 1A). Another characteristic observed in the coating at 30 min, was the surface porosity reduction when compared to the 10 min condition, due to the greater amount of globular formations (nickel and SiC) among the cobalt structures. These results indicate that the coating formed at 30 min is richer in cobalt ( Figure 2) and it has a larger grain size when compared to the 20 min condition. At 40, 50 and 60 min ( Figures 1D, 1E and 1F), the morphology and the chemical composition percentage of the surface coatings ( Figure 2) varied at each time interval with alternations between richer structures of cobalt or nickel and SiC. The increase in the cobalt content deposited on the sample surface resulted in a decrease in the other two components in the final coating, and so on. The increase in the cobalt content produces a surface with greater roughness and a larger grain size. Meanwhile, the elevation of nickel and SiC content fills the void spaces on the surface through the deposition of these components in the irregularities caused by the presence of cobalt in the previous layer and, therefore, resulting in a smaller grain size. Although there were variations in the amounts of Co, Ni and SiC deposited on the surfaces obtained after 40 min, the deposits morphology observed in Figures 1D, 1E and 1F was similar. The different morphologies obtained over the deposition time indicate that the electrodeposition of the coating occurred through the formation of layers composed mainly of cobalt or nickel, contrasting with what was expected by the anomalous codeposition, wich is a characteristic of metals in the iron group (Ni, Co e Fe) 10 . In the present work, the less noble element (cobalt), despite being in a lower proportion in the electrolytic bath (17 wt.%), did not deposit preferentially to nickel all the time. Nickel deposition is thermodynamically favored over cobalt, although their reduction potentials are close, their thermodynamics indicate that they would deposit in an approximate proportion to the concentrations in the electrolytic bath 9 . The nickel deposition occurs in a single stage, transfering electrons to the active nickel species, resulting metallic nickel, according to Equation 1 26 : Some active nickel species complex with the citrate ions present in the bath, generating another active species NiCit − , which will slowly, also provide a reduction of metallic nickel on the substrate, as described in Equation 2 presented below: With the nickel deposition, the hydrogen evolution reaction starts simultaneously as shown in Equation 3 27 : Unlike nickel, whose reduction occurs in a single phase, the deposition of cobalt occurs through a two-stage electron transfer: the first stage corresponds to the reduction of free Co 2+ ions to Co + ions and the second stage is a rapid process of reducing monovalent ions to metallic cobalt, according to Equations 4 and 5, respectively 28 : Similarly to nickel in Equation 2, some Co 2+ ions will be complexed to citrate, so that this CoCit − complex ion will favor the cobalt reduction on the surface as shown in Equation 6: Over time, CoCit − diffusive complex ions reach the electrode more slowly. The delayed reduction is also associated with purely chemical processes prior to the reduction itself, and dissociation of the adsorbed complex 9 . Although the reactions presented above indicate greater ease of nickel deposition, in Ni-Co/SiC coatings obtained within 10 min, 30 min and 50 min ( Figure 2), a highly preferential deposition of cobalt occurred. This occurrence is attributed to the formation and adsorption MOH + metal hydroxides due to the increase of pH near the cathode surface 29 . The hydrogen evolution reaction (Equation 3) causes an increase in the concentration of OH − near the surface of the cathode. Consequently, mono-metallic hydroxides MOH + are formed and adsorbed on the surface of the deposit. Since the Co 2+ ion is more reactive than the Ni +2 ion, more hydroxylated cobalt species will be formed and available to be adsorbed on the surface. Thus, the high Co content in the coating is associated with greater adsorption of ( ) According to the above reactions, it is possible to propose a multilayer formation mechanism where: (1) the initial layer of the Ni-Co/SiC nanocomposite coating obtained within 10 min of deposition is richer in cobalt and provides roughness for SiC adsorption and acts by lowering the surface energy to reduce nickel; (2) a second nickel-rich layer forms, filling the void spaces among the cobalt needles and trapping the SiC after 20 min (Figure 1-B); (3) in subsequent times, there is an alternation between layers rich in cobalt and nickelrich layers and SiC, depositing sequentially and creating conditions for the next layer to be formed by filling the void spaces and promoting the densification of the coatings.
Normally, it is expected that during the electrodeposition, the variation of cathode current influences the composition of the coatings due to different energies provided to the migration of species. However, it has found that when maintaining a constant cathodic current density of 5.5 A dm -2 and operating parameters for a conventional coating has been found that the electrodeposition process triggered a series of reactions that result in a coating formed from multiple layers, with a gradient functional. The advantage of a functionally graded coatings is the possibility of deflecting the direction of corrosion development and retarding the exposure of the substrate to the medium by sealing existing pores and defects 30 .
Analyzing Figure 3, the low intensity peaks in the range of 2θ between 20° and 40° and, specifically the peaks 42.68°; 45.72°; 75.36° and 78.05° are related to the presence of SiC with rhombohedral crystal structure. The high intensity peaks correspond to a solid two-phase solution, which is rich in Ni and Co since these active species are present in the electrolytic bath and form the composite matrix with face-centered cubic (FCC) crystalline structure. The Ni-Co matrix identified has preferential orientation (220) followed by the planes (111), (311) and (200) that correspond to the respective values of the diffraction angle 2θ of 44.46°; 76.26°; 92.62° and 51.60°. The intensity of diffraction peaks showed the opposite behavior presented by the grain size, they increase considerably when there is grain refining as observed in samples with Ni-rich matrix ( Figure 2). Similary to the grain size, the texture coefficient (TC) varied depending on the deposition time. For example, the lowest grain size value occurred on the deposited surface for 20 min, whose TC values were higher for the planes (111) and (200), which are planes with high atomic density. Additionally, the TC of the plane (220) at the 20 min sample was the lowest of all samples and this plane has the lowest atomic density. The variation in galvanostatic deposition time did not affect neither the preferential orientation plane (220) nor the FCC structure phase, although the surfaces of the deposits have different morphologies and chemical compositions. Figure 4 shows the measurements related to the thickness of Ni-Co/SiC nanocomposite coatings formed at 10, 20, 30, 40, 50 and 60 min of electrodeposition.

Cross-section characterization
In Figure 4, it can be seen that the values increase with the deposition time. According to Faraday's Law, the amount of all elements released at the cathode or anode during electrolysis is proportional to the amount of electrical charge that passes through the system from one electrode to another 6 . When there is a galvanostatic deposition and a fixed value of cathodic current density is applied on the substrate, it allows the thickness to be directly proportional to the deposition time. Furthermore, the codeposition of inert particles such as SiC, which are not reduced at the cathode, also contribute to the increase of the coating thickness, this process has been explained by a number of models. In this context, Brenner proposed a mechanism consisting of five consecutive steps for the codeposition of inert particles: (1) formation of ionic clouds in the particles; (2) the particle mass transfer by convection towards the cathode (substrate); (3) mass transfer of particles to the cathode surface by diffusion through a hydrodynamic boundary layer; (4) adsorption of the free ions and electroactive ions adsorbed on the particles in the cathode and, finally; (5) electroreduction of the adsorbed ions accompanied by the incorporation of the particles during the metallic matrix growth 31 . Guglielmi postulated that eletrocodeposition process occurs in two stages 32 . Firstly, the particles are poorly adsorbed on the cathode surface by Van der Waals forces with a high degree of surface coverage, which can be described by Langmuir adsorption isotherm. Secondly, the particles are strongly adsorbed on the surface, by Coulomb forces under the effect of the applied electric field, and incorporated by the growth of the metallic matrix. Generally, the movement of ions and particles is controlled by an electric field and by the electrolyte agitation, these parameters were kept constant in this work 4,28 . For inert SiC, the particles have to be trapped in the metal matrix, so it is necessary to form a "cloud" of cations adsorbed on the particle surface, which needs more energy than the free metal ions for convection and diffusion to the cathode surface. Furthermore, it must be considered that the deposition process of SiC particles depends on the coordination spheres formed around the surface of the nanoparticle 6 . The use of SiC nanoparticles allows a higher surface area for adsorption charge of ionic species present in the bath. Also, it favors the formation of coordination spheres around these particles. Owing to the affinity of the species (ionic or with partial polarization, in the case of water) with the SiC particle, it will present different diffusion rates to reach the substrate, depending on the type of active species involved (Co 2+ ; Ni 2+ ; H 2 O). Studies indicate that the incorporation of the ceramic phase in the coating can be improved as the most noble element is deposited, which was observed in Figure 2 2,15,20 . According Rudnik and Syrek, the "cloud" of adsorbed cation on the surface of SiC can ensure electrostatic attraction between particles and the cathode, but only the reduction of these metal ions assures permanent and stable insertion of nanoparticulate in the matrix metallic 23 . Also, according to the authors, this incorporation is seriously dependent on the current density and hydrodynamic conditions, which, in turn, determine the time of adhesion to the cathode surface, which must be sufficient for its incorporation. In the present work, the concentration of nanoparticulate SiC added to the electrolytic bath was 30 g/L. When baths with a high concentration of particles are used, there is a greater possibility that the particles will adsorb on the coating and, consequently, the deposits will have higher SiC contents 4 . However, in these baths, particle agglomeration can become a problem, as the uniform distribution of the reinforcement phase in the matrix is difficult 20 . For this reason, the electrolytic bath preparation occurred with the nanoparticles suspension in the bath through magnetic stirring for 24 hours prior to the deposition. Figure 5 shows the micrographs of the crosssection obtained by SEM after etching.
In Figure 5 it can be seen that the coatings were adhered. Moreover, they showed a uniform thickness and were formed by dense fine-grained structures. A well-defined interface between the coating and the substrate (API 5L X80 steel) is clearly seen in all samples. Along the cross-section it is possible to check the delimitation of the multiple and intermediate layers with distinct characteristics and porosities in all of the Ni-Co/SiC coating samples. It appears that these intermediate layers formed by more widely spaced lamellae were more frequent in the regions closer to the surface (coating / resin interface). This may indicate that the initially formed layer has spaced lamellae morphology. Plus, it becomes more densified and / or compacted as the upper layer is deposited. The reduction of species and the trapping of SiC contribute to the increase in the thickness of the coating and the filling of void spaces. Thus, the region closer to the coating / substrate interface presents more refined layers and a more compact morphology. As the deposition time increases, the deeper regions of the coating become more compact than the region closer to the surface. In this case, the deposition time acted both on the growth of the coating, wich probably occurred due to the densification of the layers already deposited as well as on deposition of new layers ( Figure 5), favoring the increase in thickness (Figure 4).
The observation of cross-section by SEM led to the investigation of the chemical composition of the constituent layers of the Ni-Co/SiC nanocomposite coating. The analyzes were performed along the coating with depth measurements of 10 µm, 20 µm and 30 µm and are listed in Table 3 below.
The data shown in Table 3 revealed a variation in the chemical composition of the cross-section of all samples, indicating that the SiC capture and Ni and Co deposition processes are not homogeneous and do not occur at a constant rate. This fact can be explained by the sequence of reactions triggered after the beginning of electrodeposition (Equations 1 to 7) and verified by the different surface morphologies that were obtained in the samples at different times of electrodeposition (Figure 1), maintaining the hydrodynamic and current conditions. Analyzing the chemical composition in the cross-section of each sample, the competition between Ni 2+ and Co 2+ cations is clear since, depending on the depth of the coating, there are regions where cobalt is not the element with the highest content, as would be expected by the anomalous codeposition. These results indicate that the obtained coatings have a non-homogeneous cross-section due to the presence of multiple layers, whose individual characteristics combined should reflect the chemical and mechanical properties analyzed on the surface. It is observed in Table 3 that all samples have regions where the concentration of SiC is maximum and regions where its concentration is minimal forming a functional gradient. This trend is observed in all studied samples and can be attributed to the different diffusion rates of ionic species and the particle "cloud" throughout the deposition process. A particle distribution gradient in multilayer deposits can lead to the production of improved coatings that have the ability to self-control chemical or physical properties depending on the thickness of the coating 12 . SiC nanoparticles adsorb on the surface of cobalt needle-like structures, expanding the surface area, with subsequent nickel coating, but they can also migrate to more stable sites, reducing the porosity of the coating. The use of multi-layered coatings can be an alternative to reduce porosity because the probability of pores, from different layers, coinciding is low. The increase in the thickness of the coatings layer observed in Figure 4 is also a measure of interest since thicker noble coatings protect the substrate more effectively 30 . Thus, combined with the study of thickness (Figure 4), the use of multi-layer coatings ( Figure 5) is a promising tool in several industry fields. These multi-layers have two functions: reducing the number of pores capable of exposing the substrate and changing properties, such as the corrosion mechanism 33 . In addition, it was found that the chemical compositions determined in the cross-section of the deposits (Table 3) were different from the values determined on the surface of the coatings (Figure 2). Srivastava et al. also found different chemical compositions between the cross-section and the surface of Ni-Co/SiC nanocomposite coatings 7 . Lari Baghal, Heydarzadeh Sohi and Amadeh observed a slight decrease in the cobalt content from the bottom to the surface that was associated with a slight depletion of cobalt ions in electrolyte during the electrodepositions 15 . The discovery that the chemical composition of the Ni-Co/SiC nanocomposite coating varied transversely along the cross-section is in line with what has been pointed out in several studies, which analyzed the Ni-Co/SiC nanocomposite coating as a coating formed by a single homogeneous layer, whose Ni-Co matrix has a uniform composition, but presents agglomerated regions of SiC 1,4,15,20 . Dheeraj et al. performed linear mapping using Energy Dispersive Spectroscopy (EDS) analysis on the cross-section of the Ni-Co/SiC coating obtained by pulsed electrodeposition on a copper substrate 34 . The results revealed  20 . Meanwhile, the SEM images indicated a uniform distribution of SiC agglomerates. It is noteworthy that obtaining nanocomposite coatings can be influenced by a series of parameters including particle characteristics (type, dimensions, surface charge and concentration), electrolyte composition (electrolyte concentration, surfactant type and concentration, additives, temperature and pH), current density (direct current, pulsed current, reverse pulse current, duty cycle and potentiostatic control), hydrodynamics (laminar, mixed and turbulent regimes), the characteristics of the electrodes (inert, non-inert, rotating disk electrode, rotating cylinder electrode, plate-in-tanks, parallel plate electrodes and many variations) in addition to the type of substrate 4,12 . Many tests have been carried out to investigate the parametric effects on the codeposition of nanoparticles, however, one must also consider the specific conditions restricted to each system used. A clear picture of the exact effect of the experimental parameters is often difficult to obtain due to the correlation among them. The modification in one of the deposition parameters can result in several possibilities such as different mechanical, physical and chemical characteristics 8,9,12 . As it is a low cost technique, the equipment used in electrodeposition is commonly in use, and a series of electrolytes can be used according to the substrate and the desired characteristics for the coating 6,35 . This diversification in the experiments results in an extensive variety of works that bring more and more empirical knowledge and discoveries in the area of nanocomposite coatings obtained by electrodeposition. Figure 6 shows the effect of the deposition time on microhardness and the SiC content determined on the surface of the Ni-Co/SiC nanocomposite coating.

Micro-hardness
Comparing the behavior of the micro-hardness and the SiC content of the deposits on the surface shown in Figure 6, it was observed that the two behave similarly in response to the deposition time. The micro-hardness reaches a maximum value within 20 min, followed by a decline to a minimum value within 30 min and, in the subsequent times, the values oscillated in an intermediate range. The micro-hardness determined on the substrate surface (252 HV ± 8 HV) was lower than the values found for all samples, except in the condition at 30 min. Although the samples have thicknesses ranging from 13.2 µm to 92.3 µm, as there was a uniform coverage of the substrate verified by Figure 1, the coatings presented different micro-hardness values than the substrate. Despite the coating obtained within 20 min being the second thinner (Figure 4), the values of the SiC content and microhardness ( Figure 6) were the highest among the samples, indicating that the SiC content affected more significantly micro-hardness than the thickness of the coating. The reduction in micro-hardness observed within 30 min of deposition can mean a transition from the majority of a nickel layer with a high SiC content (20 min) to a cobalt-rich one with a low SiC content (30 min). Coupled with the lower SiC content on the sample surface after 30 min, the existence of micro-voids in the deposit structure (Figure 1-C) may have directly influenced the result found. The formation of micro-voids decreases the micro-hardness of metallic matrix composite coatings, which depends mainly on the hardness of the matrix grains and the ceramic particles incorporated in the coating 8,20 . Thus, higher levels of SiC nanoparticles should produce coatings with higher micro-hardness, using the same metal grain as the Ni-Co matrix. According to Bahadormanesh and Dolati, inherent characteristics of the particles (concentration, spacing, distribution, morphologies and interfaces), the size of the dispersed phase, the structure and the mechanical properties of the matrix are factors that influence the micro-hardness of nanocomposite coatings 14 .
The behavior observed between the micro-hardness values and the SiC content of the samples surface was similar to that observed by Pereira et al., who associated the micro-hardness with the nanoparticulate SiC content in Co-Ni/SiC nanocomposite coating electrodeposited in API 5L X80 steel 16 . Bakhit analyzed the influence of the SiC particle size on the nanocomposite structure and tribological properties and found that increasing the concentration of SiC particles incorporated in the Ni-Co nanocomposite results in increased micro-hardness 36 . Srivastava et al. reported no improvement in the hardness of Ni-Co composites (68 wt.% Co) reinforced by SiC nanoparticles and the corresponding alloy (about 300 HV), despite the fact that changes in the deposit morphology were observed 7 . The authors found that the incorporation of SiC nanoparticles did not occur satisfactorily and, therefore, did not act correctly as reinforcement in the matrix. The observed correlation between micro-hardness and SiC content shown in Figure 6 is an indicative of the proper dispersion of nanoparticles in the NiCo matrix on the surface of each sample.
The chemical composition variation in the cross-section (Table 3) of the Ni-Co/SiC nanocomposite coating motivated the investigation of micro-hardness in this region and the profiles obtained are shown in Figure 7. In Figure 7, there is a fluctuation in the micro-hardness values in the cross-section of all samples that can be associated with the functional gradient of each coating (Table 2), instituted by the competition of the active species during the electrodeposition. Comparing the micro-hardness values in the regions closer to the surface to the ones closer to the substrate, it was observed that there was an increase in micro-hardness with depth in all coatings. This increase in micro-hardness in the deepest region of the coating indicates greater densification and compaction, which may be due to species migration during deposition to more energetically favorable sites 33 . Lari Baghal, Heydarzadeh Sohi and Amadeh studied the functional gradient formed in the Ni-Co/SiC nanocomposite coating electrodeposited on aluminum plates using the pulsed current technique 15 . The authors evaluated the micro-hardness profile in the cross-section of the coating and found that the size of the indentations increased as the outer edge distanced. In this case, the authors related the observed behavior to the SiC content in the cross-section, which was lower in the innermost layers of the deposit.
When comparing the micro-hardness analysis performed on the surface ( Figure 6) and on the cross-section (Figure 7) of the coatings, a significant difference is observed between the values. In general, the micro-hardness profile in the cross-section showed higher values than that measured on the surface. Considering that the measurement carried out in the cross-section made it possible to analyze each level of the coating and that the indentations were examined in the direction parallel to the surface, the value found for the surface analysis was the result of the joint contribution of each layer (composition and crystalline structure) and the presence of defects such as micro-voids and SiC agglomerates. The gradient of chemical composition (Table 2) and the microhardness profile (Figure 7) along the cross-section showed the functional gradient of the Ni-Co/SiC nanocomposite coating obtained by galvanostatic deposition, as well as the formation dynamics and the relationship among multiple layers. These factors resulted in a multilayer Ni-Co/SiC nanocomposite coating, among which the most internal showed a higher degree of densification and therefore lower density of micro-voids.

Conclusions
The potential for multi-layer formation in the nanocomposite Ni-Co/SiC electrodeposited coating on API 5L X80 steel was studied. The influence of the deposition time on the morphology, microstructure and microhardness was investigated on the surface and in the cross-section of the coatings obtained by galvanostatic deposition, in which the operational parameters of a conventional coating were maintained. SEM-EDS analyzes revealed needle-like structures, rich in cobalt, and structures with a "cauliflower" shape, rich in nickel and SiC showing that the morphology and chemical composition of the surface of the coatings varied considerably depending on the time of deposition. The formation of the Ni-Co/SiC nanocomposite coating occurred through the initial deposition of a cobalt-rich layer. Hence, this layer acted by lowering the surface energy and promoting roughness for the deposition of a layer rich in nickel, which favored the trapping of SiC nanoparticles. The phenomenon of oscillation between surfaces rich in cobalt and nickel was observed in the subsequent layers, constituting a functional coating gradient. As a result, the different Ni-Co/ SiC nanocomposite coatings produced presented a different chemical composition in the cross-section, the thickness of which was formed from dense and refined structures. The multiple and intermediate layers had different characteristics and porosity. Despite the morphological and compositional differences depending on the deposition time, the coatings obtained exhibited preferential orientation of the plane (220) and FCC phase structure. The grain size was reduced with an increase in the SiC content on the coating surface. The Vickers micro-hardness determined on the surface of the coatings showed a correlation with the SiC content and the values found in the cross-section varied according to the depth.
Keeping the cathodic current density constant at 5.5 A dm -2 and the operational parameters for obtaining a conventional nanocomposite coating, the galvanostatic electrodeposition process triggered a series of reactions that control the deposition mechanism and resulted in a Ni-Co/SiC nanocomposite coating with a functional gradient composed of multiple layers.