Improvement of Corrosion Resistance for Gray Cast Iron in Palm Biodiesel Application Using Thermoreactive Diffusion Niobium Carbide ( NbC ) Coating

Biodiesel is a renewable fuel consisting of alkyl esters, which show a higher corrosive behavior when compared with a diesel fuel. The corrosive processes by biodiesel affects the processing infrastructure of this biofuel and mechanical parts of automotives. Valves, engine blocks, and cylinder liners are gray cast iron components affected by biodiesel corrosion. The corrosion resistance of niobium carbide (NbC) coatings deposited using thermoreactive diffusion (TRD) on gray cast iron in continuous contact with diesel fuel and palm biodiesel was studied. Both coated and uncoated samples were subjected to immersion tests, cyclic oxidation at 473 K, and an electrochemical impedance spectroscopy (EIS) test. The coatings were characterized by means of scanning electron microscopy (SEM) and X-ray diffraction (XRD). Both the rate of corrosion by immersion and the resistance to polarization via EIS showed the favorable behavior of niobium carbide coatings against the corrosion of palm biodiesel. The corrosion rate on samples coated with niobium carbide was three times lower than that of the gray casting samples. These results allow the conclusion that niobium carbide coatings could be a viable alternative to lessening the corrosive effects of palm biodiesel in the applications where gray cast iron is used in continuous contact with biofuel.


Introduction
Biodiesel is a renewable fuel that is defined as a mixture of alkyl esters with fatty acids derived mainly from vegetable oils or animal fats [1,2].This fuel has become important worldwide as it is technically competitive, biodegradable, and environmentally clean when compared to fossil diesel [3,4].One of the most-used raw materials is palm oil because it has high agricultural yields in tropical regions.[5].However, several studies have found that biodiesel tends to be more corrosive than fossil diesel for materials that are in contact with biofuel throughout their life cycle [2,6].It has been demonstrated that the corrosive effect of biodiesel is a feature of the raw material used and is related to the saturation percentage of the esters, which is higher for polyunsaturated esters such as linoleate (18:02) and linolenate (18:03) [6][7][8].Unsaturated esters tend to be reactive, exhibiting characteristics of autooxidation, photo-oxidation, and high hygroscopicity that promote the corrosive processes of the biofuel [7].
The corrosion behavior of biodiesel produced with different raw materials has been evaluated including canola, palm, soy, sunflower, and other oils.The evaluation technique commonly used is static immersion, demonstrating the greater corrosive rate of biodiesel versus diesel.Kaul et al. [1] observed that biodiesel from Jatropha curcas and Salvadora produced severe corrosion on foundry iron and aluminum.It was found that biodiesel caused deterioration to the mechanical parts, and its effects accelerated considerably when the fuel oxidized or when it absorbed humidity from the environment [9].Maru et al. [10] observed in long-term immersion tests at room temperature that biodiesel derived from soybean and sunflower oils caused significant modifications to the surface finish of carbon steel.Fazal et al. [11] found a direct relationship between an increase in temperature and the corrosion rate in low-carbon steels exposed to palm biodiesel as well as the degradation of fuel properties.Fazal et al. [2] suggested that materials such as bronze, copper, steel, and aluminum were metals that reacted with the fuel and tended to corrode in contact with palm biodiesel to form sediments that increased the ionic conductivity of the fuel.Geller et al. [12] evaluated the corrosion resistances of 316 stainless steel, cast iron, copper, and brass with various percentages of biodiesel from animal fat and diesel, resulting in an increase in corrosion rate with the increase in the biodiesel content in the mixture.
Gray iron is a commonly used material in the petrochemical process, automotive, and energy transformation industry parts.This material can be found in pumps, valves, engine blocks, and cylinder liners, where they can be at high temperature, corrosion, and wear conditions.Fazal et al. [13] performed immersion tests on palm biodiesel at room temperature (288 K) for 1200 h on gray iron.They found a corrosion rate of 0.079 mpy, identified by iron oxide (FeO and Fe 2 O 3 ) on the surface.These results were confirmed through immersion tests in palm biodiesel with different inhibitors at ambient temperature where the formations of FeCO 3 , Fe 2 O 3 , Fe(OH) 2 , and Fe 2 (OH) 2 CO 3 were evidenced due to the presence of water, biodiesel, and a fraction of unsaturated esters of biodiesel [2].M'Peko et al. [14] proposed the application of electrochemical techniques in order to study the anticorrosive properties of biofuels.They evaluated biodiesel from four different raw materials (sunflower, soybean, canola, and maize) on stainless steel using the method of electrochemical impedance spectroscopy (EIS).It was observed that the polarization resistance varied with the raw material between 4.8 and 16.3 GΩ, obtaining the best behavior for sunflower biodiesel.Furthermore, they established a viable methodology for performing electrochemical analysis in highly resistive media.Additionally, Aquino [15] evaluated soybean biodiesel via EIS using support electrolytes on different metallic materials.It was found that the polarization resistance for carbon steel was 11.0 GΩ, stainless steel 12.7 GΩ, aluminum 2.1 GΩ, and copper 1.68 GΩ, confirming that electrochemical techniques are an efficient method for determining the corrosive effects produced by biofuels.Amaya et al. [16] carried out immersion tests with diesel and palm biodiesel on gray iron and found that the gray iron underwent a process of decarburization and corrosion through pitting when it was in prolonged contact with palm biodiesel.
The production of hard coatings via the thermoreactive diffusion (TRD) technique presents commercial advantages over the PVD and CVD processes as the TRD does not require sophisticated vacuum equipment, has a low processing cost, and requires economical supplies [17,18].In the literature, there has been important research about TRD for the production of niobium carbides [19], vanadium [18], and chromium [20], among others.In general, niobium carbides have been deposited on AISI, H13, M2, and D2 steels, with microstructure characterization, wear resistance, and growth kinetics studies [21][22][23][24][25]. Amaya et al. [26] reported the production of hard vanadium carbide coatings on gray iron casting via the TRD technique in bath salts, with a process temperature of 1223 K and a deposition time of 4 h, achieving layer thicknesses greater than 7 µm.
Corrosion effects of biodiesel on gray cast iron reduces the safety, lifetime, and functionality of mechanical parts.The niobium carbide deposited by the TRD process on gray iron could enhance the corrosion resistance of the substrate.This research paper explains the application of a niobium carbide coating to improve the corrosion resistance of gray cast iron.NbC coatings will be produced and characterized.Corrosion tests on gray cast iron and NbC coatings samples will be developed and the results will be compared to define if the proposed coat would be useful to protect the substrate from corrosion by biodiesel.

Materials and Methods
The fuels evaluated were diesel derived from commercial petroleum with a sulfur content of less than 500 ppm, and biodiesel obtained from palm oil through methyl transesterification with a composition of mainly 42.5% methyl ester palmitate, 40.7% methyl ester oleate, and 10% methyl ester linoleate.The total fraction of the unsaturated esters was 51.7%.Table 1 summarizes the analysis reported by the producer of palm oil biodiesel, according to specifications and test methods according to ASTM D6751-15c [27].The specimens were obtained from an unused cylinder liner of a diesel engine.This material was a G3500 grey iron (93.1% Fe, 3.45% C, and 1.66% Si) with a density of 7.21 g/cm 3 and pearlite structure with the graphite distributed uniformly.Based on the ASTM A48M standard [28], it was determined that the microstructure of the cast iron was type 30 due to presence of pearlite in the matrix and lamellar graphite type size 5 [8].
Samples of 4 cm 2 and 0.5 cm thick square substrates were obtained by refrigerated cutting.The samples were polished with abrasive papers of silicon carbide (grade 400-1500), achieving a surface free of scratches.Half of the casting samples were coated with niobium carbide in a bath of borax salts.The TRD coating process was carried out in a borax bath perfused at 1123 K at 81 wt.%; subsequently, the temperature was raised to that of the process and ferro-niobium (16%) and aluminum (3%) were added as reducing agents.The bath was performed in stainless steel containers due to its low carbon content, thus avoiding interaction with the process.The NbC coating was prepared separately at 1173 K, 1223 K, and 1273 K, at three processing times: 2, 4, and 6 h.The samples were withdrawn upon completion of the treatment time and were rapidly cooled in order to avoid passing through the temperature that causes substrate embrittlement.They were then immersed in boiling water for 30 min to remove the excess borax produced by the bath.The coating's microstructure was studied via X-ray diffraction (XRD) using an X'Pert PRO system (Panalytical, Almelo, The Netherlands) for grazing incidence with the Bragg-Brentano configuration and monochromatized CuKα radiation (1.540998 Å), working at 45 kV and 40 mA.The scan was conducted within the angular range 2θ from 25 • to 100 • with a step of 0.02 • and a monochromatic CuKa radiation of 1.594 Å.The surface morphology of the coatings deposited on the gray iron substrates, and the corrosion products and the transversal section were studied via scanning electron microscopy (SEM) using FEI QUANTA 200 equipment (Thermo Fisher Scientific, Waltham, MA, USA) operating in high vacuum and 30 KV.In addition, to verify the presence of the coating, Auger Electron Spectroscopy (AES) surface tests were performed with an Omicron Nanotechnology CMA 169 (Oxford Instruments, Abingdon, UK) with an evaluation range between 40 and 400 eV at intervals of 0.5 eV.The coating thickness was measured using a 500 optical microscope (LECO Corporation, St. Joseph, MI, USA) and the images were analyzed in the IA32 Image Analysis System (LECO Corporation, St. Joseph, MO, USA), with a magnification of 2000×.Corrosion behavior was determined using three tests: (1) an immersion test at constant temperatures of 291 K and 313 K, (2) a cyclic oxidation test with heating and cooling cycles between 291 K and 473 K for a total time of 1320 h (55 days), and (3) electrochemical impedance spectroscopy (EIS).The immersion and cyclic oxidation were done with hermetically sealed containers completely filled with fuel, with three replicates for each test.Subsequent to the immersion test, the samples were introduced into the ultrasound equipment in a solution of hydrochloric acid and tin chloride at room temperature to remove the corrosion products.The weight loss was measured according to the procedure of ASTM G31-72 [29], and the corrosion rate was evaluated using the following equation: where the corrosion rate is given in 0.001 inches per year; W is the weight lost during exposure to the corrosive medium (g); 3.45 × 10 6 is the unit conversion factor; ρ is the density (g/cm 3 ); A is the exposed surface (cm 2 ); and t is the exposure time (h) [29,30].Electrochemical impedance spectroscopy tests were also performed for the samples for a period of 144 h at 291 K using a 3-electrode electrochemical cell with a silver pseudo electrode as a reference.The electrochemical cell was constructed with one working electrode of 4 cm 2 , located in parallel to a high-density electrolytic graphite sheet, used as an auxiliary electrode.Silver wires (Ag) with a 0.5 mm diameter were used as a reference electrode.The testing sample was mounted on the working electrode and exposed to the electrolyte through an orifice with a diameter of 10 mm providing an exposure area of 78.54 mm 2 .The separation between the working electrode and reference electrode was 0.5 mm.Electrochemical measurements were performed with a Gamry-Reference 600 (Gamry Instruments, Inc., Philadelphia, PA, USA).The amplitude of the disturbing signal used was 200 mV with a frequency range of 0.00001-100 kHz.Experiments were repeated at least three times for each material evaluated and were conducted in a Faraday cage.The experimental data were acquired with the EIS300 module and analyzed using Echem Analyst software (Gamry Instruments, Inc., Philadelphia, PA, USA).

Results and Discussion
Figure 1a,b show the etched cross-section and surface morphology of the NbC coating on the substrate.The carbide layer and the gray iron were clearly defined and separated by an interface without the presence of a transition zone between the coating and the substrate.The coating exhibited a compact, continuous, and homogeneous structure with constant thickness, consistent with previous studies [13,20,21].The morphology of the coating was dependent on the carbon activity in the substrate [20].Ferrous materials with high carbon content such as gray cast iron have a relative low carbon activity, which results in low nucleation density and a poor supply of carbon atoms for the formation of carbide.Several sub-micron-sized grains produced on the substrate surface in the initial stage of the TRD process were observed [20].The coarse grains can grow from these initial grains by increasing their size and number with the increase in time to form a continuous thin layer on the gray iron surface.Then, the morphology changed with elongated grains in the direction perpendicular to the coating/substrate interface and sub-micron grains on the surface parallel to the coating/substrate interface [20].
formation of carbide.Several sub-micron-sized grains produced on the substrate surface in the initial stage of the TRD process were observed [20].The coarse grains can grow from these initial grains by increasing their size and number with the increase in time to form a continuous thin layer on the gray iron surface.Then, the morphology changed with elongated grains in the direction perpendicular to the coating/substrate interface and sub-micron grains on the surface parallel to the coating/substrate interface [20].Niobium carbide coating thicknesses ranging from 3.47 ± 0.27 to 13.81 ± 0.35 µm at 1173 K to 1273 K for 2 h and 6 h, respectively, were obtained.Figure 2 shows that the coating thickness increased with the duration of the treatment and the temperature, which is in agreement with classical kinetic theory [23,31].Based on these results, the coating system produced with a treatment time of 4 h and deposition temperature of 1223 K was selected for the corrosion tests.This treatment allows for coatings with homogeneous surfaces to be obtained with a layer thickness of 10 µm, and has a low energy cost among the treatments.Niobium carbide coating thicknesses ranging from 3.47 ± 0.27 to 13.81 ± 0.35 μm at 1173 K to 1273 K for 2 h and 6 h, respectively, were obtained.Figure 2 shows that the coating thickness increased with the duration of the treatment and the temperature, which is in agreement with classical kinetic theory [23,31].Based on these results, the coating system produced with a treatment time of 4 h and deposition temperature of 1223 K was selected for the corrosion tests.This treatment allows for coatings with homogeneous surfaces to be obtained with a layer thickness of 10 μm, and has a low energy cost among the treatments.The results obtained from the AES testing were analyzed using the database of the National Institute of Standards and Technology (NIST).The presence of mainly niobium (167 eV) and carbon (272 eV) was verified.The analysis of the atomic concentration showed 50.75% carbon for the KLL transition and 50.75% niobium for the MNN transition (Figure 3).The results obtained from the AES testing were analyzed using the database of the National Institute of Standards and Technology (NIST).The presence of mainly niobium (167 eV) and carbon (272 eV) was verified.The analysis of the atomic concentration showed 50.75% carbon for the KLL transition and 50.75% niobium for the MNN transition (Figure 3).Niobium carbide coating thicknesses ranging from 3.47 ± 0.27 to 13.81 ± 0.35 μm at 1173 K to 1273 K for 2 h and 6 h, respectively, were obtained.Figure 2 shows that the coating thickness increased with the duration of the treatment and the temperature, which is in agreement with classical kinetic theory [23,31].Based on these results, the coating system produced with a treatment time of 4 h and deposition temperature of 1223 K was selected for the corrosion tests.This treatment allows for coatings with homogeneous surfaces to be obtained with a layer thickness of 10 μm, and has a low energy cost among the treatments.The results obtained from the AES testing were analyzed using the database of the National Institute of Standards and Technology (NIST).The presence of mainly niobium (167 eV) and carbon (272 eV) was verified.The analysis of the atomic concentration showed 50.75% carbon for the KLL transition and 50.75% niobium for the MNN transition (Figure 3).   Figure 5 shows the results of the corrosion rate for the samples submerged in the diesel and biodiesel fuels.It was observed that diesel fuel caused a lower corrosion rate for each material.The niobium carbide coating led to a reduction of three times in the corrosion rate of the two fuels, considering the three temperature regimes of the test: 291 K, 313 K, and cyclic oxidation.Furthermore, in the cyclic oxidation test, the coating submerged in biodiesel had a better performance (0.78 mpy) when compared to the diesel-submerged cast iron (0.80 mpy), indicating a higher durability of the components used in this type of application than the material traditionally used.In general, it was observed that with an increase in temperature, the speed of corrosion of the samples accelerated.The corrosive effect was greater for the case of diesel in the cyclic oxidation test, which could be associated with the greater activity of the sulfur molecules; this is the main cause of corrosion by this fuel and it is absent in the case of palm biodiesel [32].Field Emission Gun Scanning Electron Microscope (SEM-FEG) was used to analyze the morphology of the surface after the process of corrosion by static immersion.The most representative micrographs of smelting and coating are shown in Figure 6, after an exposure of 1320 h and a cyclic oxidation (OC) state.The gray iron showed a partial loss of graphite through the grooves produced by a process of selective corrosion of the ferrite phase of the pearlite structure.Surface pitting was also observed, with sizes ranging from 20 to 100 μm and smaller sizes (±2 μm) distributed randomly on the surface (Figure 6a). Figure 6b shows the niobium carbide coating, where there was neither representative pitting on the surface nor corrosion on a large scale.Figure 7 shows the surface of the coating at a higher magnification, which allowed the identification of the intergranular oxide growth in small quantities.Figure 5 shows the results of the corrosion rate for the samples submerged in the diesel and biodiesel fuels.It was observed that diesel fuel caused a lower corrosion rate for each material.The niobium carbide coating led to a reduction of three times in the corrosion rate of the two fuels, considering the three temperature regimes of the test: 291 K, 313 K, and cyclic oxidation.Furthermore, in the cyclic oxidation test, the coating submerged in biodiesel had a better performance (0.78 mpy) when compared to the diesel-submerged cast iron (0.80 mpy), indicating a higher durability of the components used in this type of application than the material traditionally used.In general, it was observed that with an increase in temperature, the speed of corrosion of the samples accelerated.The corrosive effect was greater for the case of diesel in the cyclic oxidation test, which could be associated with the greater activity of the sulfur molecules; this is the main cause of corrosion by this fuel and it is absent in the case of palm biodiesel [32].Figure 5 shows the results of the corrosion rate for the samples submerged in the diesel and biodiesel fuels.It was observed that diesel fuel caused a lower corrosion rate for each material.The niobium carbide coating led to a reduction of three times in the corrosion rate of the two fuels, considering the three temperature regimes of the test: 291 K, 313 K, and cyclic oxidation.Furthermore, in the cyclic oxidation test, the coating submerged in biodiesel had a better performance (0.78 mpy) when compared to the diesel-submerged cast iron (0.80 mpy), indicating a higher durability of the components used in this type of application than the material traditionally used.In general, it was observed that with an increase in temperature, the speed of corrosion of the samples accelerated.The corrosive effect was greater for the case of diesel in the cyclic oxidation test, which could be associated with the greater activity of the sulfur molecules; this is the main cause of corrosion by this fuel and it is absent in the case of palm biodiesel [32].Field Emission Gun Scanning Electron Microscope (SEM-FEG) was used to analyze the morphology of the surface after the process of corrosion by static immersion.The most representative micrographs of smelting and coating are shown in Figure 6, after an exposure of 1320 h and a cyclic oxidation (OC) state.The gray iron showed a partial loss of graphite through the grooves produced by a process of selective corrosion of the ferrite phase of the pearlite structure.Surface pitting was also observed, with sizes ranging from 20 to 100 μm and smaller sizes (±2 μm) distributed randomly on the surface (Figure 6a). Figure 6b shows the niobium carbide coating, where there was neither representative pitting on the surface nor corrosion on a large scale.Figure 7 shows the surface of the coating at a higher magnification, which allowed the identification of the intergranular oxide growth in small quantities.Field Emission Gun Scanning Electron Microscope (SEM-FEG) was used to analyze the morphology of the surface after the process of corrosion by static immersion.The most representative micrographs of smelting and coating are shown in Figure 6, after an exposure of 1320 h and a cyclic oxidation (OC) state.The gray iron showed a partial loss of graphite through the grooves produced by a process of selective corrosion of the ferrite phase of the pearlite structure.Surface pitting was also observed, with sizes ranging from 20 to 100 µm and smaller sizes (±2 µm) distributed randomly on the surface (Figure 6a). Figure 6b shows the niobium carbide coating, where there was neither representative pitting on the surface nor corrosion on a large scale.Figure 7 shows the surface of the coating at a higher magnification, which allowed the identification of the intergranular oxide growth in small quantities.The X-ray patterns made by the iron smelter before and after the biodiesel corrosion process are shown in Figure 8.The analysis allowed the identification of new peaks associated with Fe2O3 (hematite), Fe3O4 (magnetite), and FeO(OH) (goethite) [3]. Figure 9 shows the X-ray pattern of the niobium carbide coating prior and after exposure to biodiesel.The presence of additional peaks related to NbO, NbO2, and Nb2O5 was observed.The diffractograms showed that the two surfaces interacted with the biodiesel and that different species of oxides appeared, which were produced during the corrosion process [24].The X-ray patterns made by the iron smelter before and after the biodiesel corrosion process are shown in Figure 8.The analysis allowed the identification of new peaks associated with Fe2O3 (hematite), Fe3O4 (magnetite), and FeO(OH) (goethite) [3]. Figure 9 shows the X-ray pattern of the niobium carbide coating prior and after exposure to biodiesel.The presence of additional peaks related to NbO, NbO2, and Nb2O5 was observed.The diffractograms showed that the two surfaces interacted with the biodiesel and that different species of oxides appeared, which were produced during the corrosion process [24].The X-ray patterns made by the iron smelter before and after the biodiesel corrosion process are shown in Figure 8.The analysis allowed the identification of new peaks associated with Fe 2 O 3 (hematite), Fe 3 O 4 (magnetite), and FeO(OH) (goethite) [3]. Figure 9 shows the X-ray pattern of the niobium carbide coating prior and after exposure to biodiesel.The presence of additional peaks related to NbO, NbO 2 , and Nb 2 O 5 was observed.The diffractograms showed that the two surfaces interacted with the biodiesel and that different species of oxides appeared, which were produced during the corrosion process [24].The X-ray patterns made by the iron smelter before and after the biodiesel corrosion process are shown in Figure 8.The analysis allowed the identification of new peaks associated with Fe2O3 (hematite), Fe3O4 (magnetite), and FeO(OH) (goethite) [3]. Figure 9 shows the X-ray pattern of the niobium carbide coating prior and after exposure to biodiesel.The presence of additional peaks related to NbO, NbO2, and Nb2O5 was observed.The diffractograms showed that the two surfaces interacted with the biodiesel and that different species of oxides appeared, which were produced during the corrosion process [24].Figure 10 shows the Nyquist diagrams obtained from the electrochemical impedance test performed on the niobium carbide coating submerged in biodiesel at a temperature of 291 ± 2 K with immersion times of 1 h, 24 h, 48 h, and 144 h.It was observed that the diagram was composed of two overlapping semicircles, suggesting the presence of two constant phase elements corresponding to two electrolyte-electrode interphases.The first, at high frequencies and a larger radius, is usually associated with the resistive-capacitive behavior of the coating; and the second time constant was related to the electrolyte-substrate interface due to the pores in the coating [24,25].The polarization resistance decreased from 1.48 × 10 10 Ω to 8.95 × 10 9 Ω with an increase in the immersion time.This could be explained by the corrosive solution penetrating through the coating defects to the substrate surface.Figure 11 shows the Nyquist diagrams obtained for the niobium carbide coating when compared to the substrate in contact with diesel fuel and biodiesel for 144 h of exposure time.It was observed that the gray iron diagram was composed of a time constant that corresponded to the resistivecapacitive behavior of the substrate double layer, which agreed with the results reported by M'Peko et al. [14], while the coating was composed of two semicircles, as already mentioned.The NbC coating exhibited greater resistance to polarization when compared to the gray iron with respect to the two evaluated fuels.Likewise, the evaluated materials exhibited a lower corrosion resistance in the biodiesel, which showed a greater reactivity of the unsaturated methyl ester in the fuel.The results obtained via EIS were in agreement with those obtained in the immersion tests, proving their effectiveness in reducing the corrosive effects of the biofuel.Figure 10 shows the Nyquist diagrams obtained from the electrochemical impedance test performed on the niobium carbide coating submerged in biodiesel at a temperature of 291 ± 2 K with immersion times of 1 h, 24 h, 48 h, and 144 h.It was observed that the diagram was composed of two overlapping semicircles, suggesting the presence of two constant phase elements corresponding to two electrolyte-electrode interphases.The first, at high frequencies and a larger radius, is usually associated with the resistive-capacitive behavior of the coating; and the second time constant was related to the electrolyte-substrate interface due to the pores in the coating [24,25].The polarization resistance decreased from 1.48 × 10 10 Ω to 8.95 × 10 9 Ω with an increase in the immersion time.This could be explained by the corrosive solution penetrating through the coating defects to the substrate surface.Figure 10 shows the Nyquist diagrams obtained from the electrochemical impedance test performed on the niobium carbide coating submerged in biodiesel at a temperature of 291 ± 2 K with immersion times of 1 h, 24 h, 48 h, and 144 h.It was observed that the diagram was composed of two overlapping semicircles, suggesting the presence of two constant phase elements corresponding to two electrolyte-electrode interphases.The first, at high frequencies and a larger radius, is usually associated with the resistive-capacitive behavior of the coating; and the second time constant was related to the electrolyte-substrate interface due to the pores in the coating [24,25].The polarization resistance decreased from 1.48 × 10 10 Ω to 8.95 × 10 9 Ω with an increase in the immersion time.This could be explained by the corrosive solution penetrating through the coating defects to the substrate surface.Figure 11 shows the Nyquist diagrams obtained for the niobium carbide coating when compared to the substrate in contact with diesel fuel and biodiesel for 144 h of exposure time.It was observed that the gray iron diagram was composed of a time constant that corresponded to the resistivecapacitive behavior of the substrate double layer, which agreed with the results reported by M'Peko et al. [14], while the coating was composed of two semicircles, as already mentioned.The NbC coating exhibited greater resistance to polarization when compared to the gray iron with respect to the two evaluated fuels.Likewise, the evaluated materials exhibited a lower corrosion resistance in the biodiesel, which showed a greater reactivity of the unsaturated methyl ester in the fuel.The results obtained via EIS were in agreement with those obtained in the immersion tests, proving their  behavior of the substrate double layer, which agreed with the results reported by M'Peko et al. [14], while the coating was composed of two semicircles, as already mentioned.The NbC coating exhibited greater resistance to polarization when compared to the gray iron with respect to the two evaluated fuels.Likewise, the evaluated materials exhibited a lower corrosion resistance in the biodiesel, which showed a greater reactivity of the unsaturated methyl ester in the fuel.The results obtained via EIS were in agreement with those obtained in the immersion tests, proving their effectiveness in reducing the corrosive effects of the biofuel.Figure 12 shows the values of the polarization resistance for the coating and the substrate in the corrosive environments of diesel and biodiesel as a function of the immersion time.It was observed that the coated samples exhibited higher polarization resistance with respect to gray iron throughout the evaluation period, being three times higher when the test was done in biodiesel and 1.4 times in diesel.The higher corrosion rate or less polarization resistance measured in the biodiesel-gray iron system may correspond to greater reactivity and the formation of iron oxides, according to the mechanism proposed by Aquino [15].This corrosive process occurs simultaneously with the biodiesel processes, which degrade the fuel and produce aldehydes, carboxylic acids, alcohols, sediments, and insoluble gums [33].The coating anticorrosive properties are associated with the ceramic structure of NbC, with the cubic structure requiring higher energies in order to be transformed into corrosion products.The corrosion properties observed in the NbC coatings have been studied in previous works by Orjuela et al. [25] and Fernandez et al. [34], who evaluated corrosion behavior in saline atmospheres and obtained satisfactory results similar to those obtained in this research.

Conclusions
The results of the corrosion tests using immersion and electrochemical impedance spectroscopy showed that niobium carbide coatings offer high anticorrosive properties for protection from degradation in environments of palm biodiesel when compared to gray iron.Figure 12 shows the values of the polarization resistance for the coating and the substrate in the corrosive environments of diesel and biodiesel as a function of the immersion time.It was observed that the coated samples exhibited higher polarization resistance with respect to gray iron throughout the evaluation period, being three times higher when the test was done in biodiesel and 1.4 times in diesel.The higher corrosion rate or less polarization resistance measured in the biodiesel-gray iron system may correspond to greater reactivity and the formation of iron oxides, according to the mechanism proposed by Aquino [15].This corrosive process occurs simultaneously with the biodiesel autooxidation processes, which degrade the fuel and produce aldehydes, carboxylic acids, alcohols, sediments, and insoluble gums [33].The coating anticorrosive properties are associated with the ceramic structure of NbC, with the cubic structure requiring higher energies in order to be transformed into corrosion products.The corrosion properties observed in the NbC coatings have been studied in previous works by Orjuela et al. [25] and Fernandez et al. [34], who evaluated corrosion behavior in saline atmospheres and obtained satisfactory results similar to those obtained in this research.Figure 12 shows the values of the polarization resistance for the coating and the substrate in the corrosive environments of diesel and biodiesel as a function of the immersion time.It was observed that the coated samples exhibited higher polarization resistance with respect to gray iron throughout the evaluation period, being three times higher when the test was done in biodiesel and 1.4 times in diesel.The higher corrosion rate or less polarization resistance measured in the biodiesel-gray iron system may correspond to greater reactivity and the formation of iron oxides, according to the mechanism proposed by Aquino [15].This corrosive process occurs simultaneously with the biodiesel autooxidation processes, which degrade the fuel and produce aldehydes, carboxylic acids, alcohols, sediments, and insoluble gums [33].The coating anticorrosive properties are associated with the ceramic structure of NbC, with the cubic structure requiring higher energies in order to be transformed into corrosion products.The corrosion properties observed in the NbC coatings have been studied in previous works by Orjuela et al. [25] and Fernandez et al. [34], who evaluated corrosion behavior in saline atmospheres and obtained satisfactory results similar to those obtained in this research.

Conclusions
The results of the corrosion tests using immersion and electrochemical impedance spectroscopy showed that niobium carbide coatings offer high anticorrosive properties for protection from degradation in environments of palm biodiesel when compared to gray iron.

Conclusions
The results of the corrosion tests using immersion and electrochemical impedance spectroscopy showed that niobium carbide coatings offer high anticorrosive properties for protection from degradation in environments of palm biodiesel when compared to gray iron.
From the immersion tests, it was determined that the corrosion rates in the biodiesel test was three times lower for the coated samples due to the ceramic structure.The SEM and XRD tests showed severe effects of pitting corrosion in the grey iron with the presence of Fe 2 O 3 , Fe 3 O 4 , and FeO(OH), while the NbC coatings exhibited effects of intergranular corrosion in the grain boundaries with the presence of NbO, NbO 2 , and Nb 2 O 5 .These results allowed the conclusion that NbC coatings on gray iron act as protection against corrosion by palm biodiesel.

Figure 2 .
Figure 2. NbC coating thickness vs. time TRD at various treatment temperatures.

Figure 3 .
Figure 3. AES spectrum of NbC 1223 K for 4 h.XRD analysis of the carbide layer produced on the gray cast iron at 1223 K for 4 h is shown in Figure4.The cubic phase of NbC was confirmed according to the JCPDS 00 038 1364 card, showing high intensity peaks with a mixed orientation of mainly crystal planes (111), (200), (220), and (311).No significant effect of the composition of the salt bath or the substrate was observed in the orientations observed.NbC had a cubic crystal structure similar to NaCl (Fm3m) and space group number 225.

Figure 2 .
Figure 2. NbC coating thickness vs. time TRD at various treatment temperatures.

Figure 2 .
Figure 2. NbC coating thickness vs. time TRD at various treatment temperatures.

Figure 3 .
Figure 3. AES spectrum of NbC 1223 K for 4 h.XRD analysis of the carbide layer produced on the gray cast iron at 1223 K for 4 h is shown in Figure4.The cubic phase of NbC was confirmed according to the JCPDS 00 038 1364 card, showing high intensity peaks with a mixed orientation of mainly crystal planes (111), (200), (220), and (311).No significant effect of the composition of the salt bath or the substrate was observed in the orientations observed.NbC had a cubic crystal structure similar to NaCl (Fm3m) and space group number 225.

Figure 4 .
Figure 4. XRD spectrum of gray cast iron and NbC coating for 4 h at 1223 K.

Figure 5 .
Figure 5. Corrosion rates of the gray cast iron and NbC coating in diesel and biodiesel.

Figure 4 .
Figure 4. XRD spectrum of gray cast iron and NbC coating for 4 h at 1223 K.

Figure 4 .
Figure 4. XRD spectrum of gray cast iron and NbC coating for 4 h at 1223 K.

Figure 5 .
Figure 5. Corrosion rates of the gray cast iron and NbC coating in diesel and biodiesel.

Figure 5 .
Figure 5. Corrosion rates of the gray cast iron and NbC coating in diesel and biodiesel.

Figure 6 .
Figure 6.SEM-FEG micrograph on the surface exposed to palm biodiesel by 1320 h.(a) Gray cast iron and (b) NbC coating.

Figure 7 .
Figure 7. SEM-FEG Micrograph of NbN coating exposed to palm biodiesel at 1320 h.

Figure 8 .
Figure 8. XRD spectrum of the gray cast iron before and after exposure to palm biodiesel at 1320 h in OC.

Figure 6 .Figure 6 .
Figure 6.SEM-FEG micrograph on the surface exposed to palm biodiesel by 1320 h.(a) Gray cast iron and (b) NbC coating.

Figure 7 .
Figure 7. SEM-FEG Micrograph of NbN coating exposed to palm biodiesel at 1320 h.

Figure 8 .
Figure 8. XRD spectrum of the gray cast iron before and after exposure to palm biodiesel at 1320 h in OC.

Figure 7 .
Figure 7. SEM-FEG Micrograph of NbN coating exposed to palm biodiesel at 1320 h.

Figure 8 .
Figure 8. XRD spectrum of the gray cast iron before and after exposure to palm biodiesel at 1320 h in OC.

Figure 8 . 11 Figure 9 .
Figure 8. XRD spectrum of the gray cast iron before and after exposure to palm biodiesel at 1320 h in OC.Coatings 2018, 8, x FOR PEER REVIEW 8 of 11

Figure 10 .
Figure 10.Nyquist diagrams obtained via EIS on the niobium carbide coating in contact with palm biodiesel at 291 ± 2 K at different exposure times.

Figure 9 .
Figure 9. XRD spectrum of the NbC coating before and after exposure to palm biodiesel at 1320 h in OC.

Coatings 2018, 8 , 11 Figure 9 .
Figure 9. XRD spectrum of the NbC coating before and after exposure to palm biodiesel at 1320 h in OC.

Figure 10 .
Figure 10.Nyquist diagrams obtained via EIS on the niobium carbide coating in contact with palm biodiesel at 291 ± 2 K at different exposure times.

Figure 10 .
Figure 10.Nyquist diagrams obtained via EIS on the niobium carbide coating in contact with palm biodiesel at 291 ± 2 K at different exposure times.

Figure 11
Figure11shows the Nyquist diagrams obtained for the niobium carbide coating when compared to the substrate in contact with diesel fuel and biodiesel for 144 h of exposure time.It was observed that the gray iron diagram was composed of a time constant that corresponded to the resistive-capacitive

Coatings 2018, 8 , 11 Figure 11 .
Figure 11.Nyquist diagrams obtained via EIS for smelting iron and niobium carbide coating in contact with diesel and palm biodiesel at 291 ± 2 K and 144 h.

Figure 12 .
Figure 12.Polarization resistance obtained from the Nyquist diagrams via EIS on the cast iron and niobium carbide coating in contact with the diesel and palm biodiesel at 291 ± 2 K.

Figure 11 .
Figure 11.Nyquist diagrams obtained via EIS for smelting iron and niobium carbide coating in contact with diesel and palm biodiesel at 291 ± 2 K and 144 h.

Coatings 2018, 8 , 11 Figure 11 .
Figure 11.Nyquist diagrams obtained via EIS for smelting iron and niobium carbide coating in contact with diesel and palm biodiesel at 291 ± 2 K and 144 h.

Figure 12 .
Figure 12.Polarization resistance obtained from the Nyquist diagrams via EIS on the cast iron and niobium carbide coating in contact with the diesel and palm biodiesel at 291 ± 2 K.

Figure 12 .
Figure 12.Polarization resistance obtained from the Nyquist diagrams via EIS on the cast iron and niobium carbide coating in contact with the diesel and palm biodiesel at 291 ± 2 K.

Table 1 .
Analysis report of palm biodiesel.