Inﬂuence of Graphite Morphology on Phase, Microstructure, and Properties of Hot Dipping and Di ﬀ usion Aluminizing Coating on Flake / Spheroidal Graphite Cast Iron

: The inﬂuence of graphite morphology on the phase, microstructure and properties of hot dipping and di ﬀ usion aluminizing (HDDA) coating on ﬂake / spheroidal graphite cast iron (FC / FCD) was investigated. The microstructure and properties of the HDDA coatings on FC / FCD were determined by the graphite morphology. The outer and inner layers of the HDDA coating comprised the Fe 2 Al 5 and FeAl phases, respectively. The outer layer of HDDA on FCD was dense and uniform; however, some pores of di ﬀ erent sizes were found in the outer coating on FC, resulting in looser HDDA coating. Hence, the wear resistance of the HDDA coating on FC was worse than that of the coating on FCD. During oxidation, many continuous oxidation channels were formed from the coating surface to the matrix in the HDDA coating on FC, resulting in the oxidation of graphite in the HDDA coating and the matrix. However, only exposed spheroidal graphite was oxidized in the HDDA coating on FCD. Thus, the high-temperature oxidation resistance of the HDDA coating on FC was also worse than that of the coating on FCD.


Introduction
The valve guide is an important part of engines and a major index for evaluating engine performance. In general, the valve guide is made of cast iron due to its better castability and machinability, and lower cost than steels with similar mechanical properties [1]. Because of the long-term operation of engines, the resistance to high-temperature oxidation and wear is required for the inner wall of the valve guide [2]. Although the wear resistance of high-phosphorus (0.35-0.65 wt.% P) cast iron is better than that of ordinary cast iron [3], the high-temperature oxidation resistance of high-phosphorus cast iron cannot meet engine demands. Surface treatment technology not only modifies the surface properties of cast iron effectively, but also maintains the original excellent mechanical properties of the matrix.
At present, the main surface treatment technologies for improving resistance to high-temperature oxidation and wear are hot-dip aluminizing [4], micro-arc oxidation (MAO) [5], thermal spraying [6], pack-aluminizing [7], and hot dipping and diffusion aluminizing (HDDA) [8]. Hot-dip aluminizing can improve oxidation resistance, and MAO coating on hot-dip aluminized cast iron improves both oxidation resistance and wear resistance. However, when the oxidation temperature is higher than

HDDA Process
The HDDA process included hot-dip aluminizing and diffusion. The specimens for hot-dip aluminizing were cleaned ultrasonically in 10 wt.% NaOH (AR, Tianjin Damao Chemical Reagent Factory, Tianjin, China) solution, deionized water, 20 vol.% HCl (AR, Tianjin Fuqi Chemical Reagent Co. Ltd., Tianjin, China) solution and deionized water at 25 • C for 3 min each, then fluxed in a mixed solution of 6 wt.% KF (AR, Tianjin Jizhun Chemical Reagent Co. Ltd., Tianjin, China) and 4 wt.% NaCl (AR, Tianjin Fengchuan Reagent Technologies Co. Ltd., Tianjin, China) at 100 • C for 5 min. During the aluminizing process, the samples were dried and preheated at 200 • C for 2 min, then immersed in a molten aluminum bath (purity > 99.7%) at 730 • C for 5 min in a well-type electrical resistance furnace (SG2-5-10, Tianjin Zhonghuan, Tianjin, China). After hot-dip aluminizing, the samples were air-cooled to room temperature. Finally, the diffusion of specimens was conducted at 950 • C in static air for 1 h. Then, the samples were cooled in a box-type furnace (FURNACE 1300 • C, Tianjin Zhonghuan, Tianjin, China).

High-Temperature Oxidation
Isothermal oxidation was performed to study the high-temperature oxidation behavior of the HDDA coating on FC/FCD. The samples were placed in a non-reactive alumina crucible. Isothermal oxidation was conducted at 750 • C in static air for 12 to 72 h. Then, crucibles containing the samples were cooled to room temperature in air. The masses of specimens were measured using a precision electronic balance (0.1 mg accuracy) after the oxidation experiment. The weight change per unit area of three specimens was averaged for each set of experimental conditions.

Wear Resistance
The Vickers hardness of FC/FCD with and without HDDA was measured by a microhardness tester (HMV-2T, Ningbo Op Instruments Co. Ltd., Ningbo, China) at a load of 980 mN for 15 s. The wear resistance of HDDA coating on FC/FCD was evaluated on a ball-on-disc tribometer (SFT-2M, Lanzhou Zhongkekaihua, Lanzhou, China) by sliding Si 3 N 4 balls (2 mm diameter) against the specimens with a load of 8 N, sliding speed of 400 r/min, sliding track diameter of 4 mm, and duration of 20 min in air [15]. The 3D morphology of the wear track profile was observed using a metallographic microscope (DSX510, Hongkong OLYMPUS, Hongkong, China).

Microstructure and Phase Analyses
The cross-sectional and surface microstructure of the HDDA coating was examined by a Hitachi S-4800 field-emission scanning electron microscope (SEM, Suzhou Seins Instrument Co. Ltd., Suzhou, China) with energy-dispersive spectrometry (EDS). The cross-section was polished using 400 #, 800 #, 1200 #, 1500 # and 2000 # SiC paper, then polished with a polishing cloth, and corroded 1-2 s. The phase composition of the HDDA coating was analyzed by a Rigaku DMAX-RC X-ray diffraction (XRD, Brook AXS Co. Ltd., Germany) system with Cu Kα radiation. The phase composition of the inner layer was analyzed by grinding the outer layer with SiC paper and performing XRD afterward.

Results and Discussion
3.1. Microstructure and Phase of the Hot-Dip Aluminide Coating Figure 1 shows the microstructure of hot-dip aluminide coating on FC/FCD hot-dip aluminized at 730 • C for 5 min. According to the EDS (EDS analysis of needles at 3 and 6 locations is performed at 10,000 times) in Table 2 (EDS spectra in Figure 2) and the XRD results in Figure 3, the aluminide coatings on FC and FCD consist of an outer Al topcoat and inner Fe 2 Al 5 coating, and FeAl 3 is distributed in the outer Al topcoat in bulk and rod forms. These are consistent with the results reported by Lin et al. [13] and Zhang et al. [16]. From Figure 1, we can observe that the inner Fe 2 Al 5 intermetallic coating of aluminized FCD grows inward as a tongue-like structure perpendicular to the matrix. However, the interface between the Fe 2 Al 5 coating and FC matrix is fairly smooth and the Fe 2 Al 5 intermetallic coating on aluminized FC (110 µm) is thicker than that on the aluminized FCD (70 µm). Because Si inhibits the diffusion of Al atoms, these differences are due to the higher Si content in FCD than that in FC [17,18]. It is clear that flaky/spheroidal graphite can prevent the growth of the intermetallic coating, as shown in Figure 1a,b.

High-Temperature Oxidation
Isothermal oxidation was performed to study the high-temperature oxidation behavior of the HDDA coating on FC/FCD. The samples were placed in a non-reactive alumina crucible. Isothermal oxidation was conducted at 750 °C in static air for 12 to 72 h. Then, crucibles containing the samples were cooled to room temperature in air. The masses of specimens were measured using a precision electronic balance (0.1 mg accuracy) after the oxidation experiment. The weight change per unit area of three specimens was averaged for each set of experimental conditions.

Wear Resistance
The Vickers hardness of FC/FCD with and without HDDA was measured by a microhardness tester (HMV-2T, Ningbo Op Instruments Co. Ltd., Ningbo, China) at a load of 980 mN for 15 s. The wear resistance of HDDA coating on FC/FCD was evaluated on a ball-on-disc tribometer (SFT-2M, Lanzhou Zhongkekaihua, Lanzhou, China) by sliding Si3N4 balls (2 mm diameter) against the specimens with a load of 8 N, sliding speed of 400 r/min, sliding track diameter of 4 mm, and duration of 20 min in air [15]. The 3D morphology of the wear track profile was observed using a metallographic microscope (DSX510, Hongkong OLYMPUS, Hongkong, China).

Microstructure and Phase Analyses
The cross-sectional and surface microstructure of the HDDA coating was examined by a Hitachi S-4800 field-emission scanning electron microscope (SEM, Suzhou Seins Instrument Co. Ltd., Suzhou, China) with energy-dispersive spectrometry (EDS). The cross-section was polished using 400 #, 800 #, 1200 #, 1500 # and 2000 # SiC paper, then polished with a polishing cloth, and corroded 1-2 s. The phase composition of the HDDA coating was analyzed by a Rigaku DMAX-RC X-ray diffraction (XRD, Brook AXS Co. Ltd., Germany) system with Cu Kα radiation. The phase composition of the inner layer was analyzed by grinding the outer layer with SiC paper and performing XRD afterward. Figure 1 shows the microstructure of hot-dip aluminide coating on FC/FCD hot-dip aluminized at 730 °C for 5 min. According to the EDS (EDS analysis of needles at 3 and 6 locations is performed at 10,000 times) in Table 2 (EDS spectra in Figure 2) and the XRD results in Figure 3, the aluminide coatings on FC and FCD consist of an outer Al topcoat and inner Fe2Al5 coating, and FeAl3 is distributed in the outer Al topcoat in bulk and rod forms. These are consistent with the results reported by Lin et al. [13] and Zhang et al. [16]. From Figure 1, we can observe that the inner Fe2Al5 intermetallic coating of aluminized FCD grows inward as a tongue-like structure perpendicular to the matrix. However, the interface between the Fe2Al5 coating and FC matrix is fairly smooth and the Fe2Al5 intermetallic coating on aluminized FC (110 µm) is thicker than that on the aluminized FCD (70 µm). Because Si inhibits

Microstructure and Phase of the HDDA Coating
Cross-sectional micrographs of HDDA coatings on FC and FCD diffused at 950 °C for 1 h after hot-dip aluminizing are shown in Figure 4a,b. Phase transformation occurs in hot-dip aluminide coating after diffusion, but the HDDA coatings on FC and FCD still consist of two layers. According to the EDS results in Table 3 (EDS spectra in Fig. 5a-d) and the XRD profile in Figure 6a,b, the Fe2Al5/FeAl phase is observed on all outer/inner coatings of the two matrixes. The α-Al2O3 coating is formed by the reaction between the Al atoms on the surface of the HDDA coating and oxygen in the air at high temperature. It cannot be observed in the cross-sectional micrographs due to its small thickness [19]. The interface between the outer and inner coatings, and that between the inner coating and FC, are smooth, because the Si content of FC is less than that of FCD. Furthermore, a larger amount of flaky graphite is found throughout the HDDA coating on FC. However, spheroidal graphite is embedded in the HDDA coating, as shown in Figure 4b. Apparently, the outer coating of HDDA on FCD is dense and uniform. Nevertheless, some pores of different sizes are observed in the outer coating of HDDA on FC. The graphite morphology in FC and FCD is similar to agaric-like flake and spheroidal morphology, respectively. Spherical graphite crystals are independent of one another, but flaky graphite crystals interact with one another. The exposed flaky graphite will be oxidized during diffusion, resulting in the oxidation of adjoining graphite crystals. Thus, some pores formed by oxidation of the tip of flake graphite are found around the flaky graphite throughout the HDDA coating. Some needles are observed in the inner coatings of the HDDA on FC and FCD, of which the growth direction is parallel to the interface between the outer and inner coatings, as shown in Figure  4c,d. According to the EDS results in Table 3 (EDS spectra in Figure 5e,f), the phase of the needles in the inner coatings of the HDDA on FC/FCD is FeAl2 phase.

Microstructure and Phase of the HDDA Coating
Cross-sectional micrographs of HDDA coatings on FC and FCD diffused at 950 • C for 1 h after hot-dip aluminizing are shown in Figure 4a,b. Phase transformation occurs in hot-dip aluminide coating after diffusion, but the HDDA coatings on FC and FCD still consist of two layers. According to the EDS results in Table 3 (EDS spectra in Figure 5a-d) and the XRD profile in Figure 6a,b, the Fe 2 Al 5 /FeAl phase is observed on all outer/inner coatings of the two matrixes. The α-Al 2 O 3 coating is formed by the reaction between the Al atoms on the surface of the HDDA coating and oxygen in the air at high temperature. It cannot be observed in the cross-sectional micrographs due to its small thickness [19]. The interface between the outer and inner coatings, and that between the inner coating and FC, are smooth, because the Si content of FC is less than that of FCD. Furthermore, a larger amount of flaky graphite is found throughout the HDDA coating on FC. However, spheroidal graphite is embedded in the HDDA coating, as shown in Figure 4b. Apparently, the outer coating of HDDA on FCD is dense and uniform. Nevertheless, some pores of different sizes are observed in the outer coating of HDDA on FC. The graphite morphology in FC and FCD is similar to agaric-like flake and spheroidal morphology, respectively. Spherical graphite crystals are independent of one another, but flaky graphite crystals interact with one another. The exposed flaky graphite will be oxidized during diffusion, resulting in the oxidation of adjoining graphite crystals. Thus, some pores formed by oxidation of the tip of flake graphite are found around the flaky graphite throughout the HDDA coating. Some needles are observed in the inner coatings of the HDDA on FC and FCD, of which the growth direction is parallel to the interface between the outer and inner coatings, as shown in Figure 4c,d. According to the EDS results in Table 3 (EDS spectra in Figure 5e,f), the phase of the needles in the inner coatings of the HDDA on FC/FCD is FeAl 2 phase.        Figure 7a shows the oxidation kinetic curves of the FC/FCD with and without HDDA coating in air at 750 °C. The weight change per unit area of FC/FCD is higher than that of HDDA FC/FCD. This result indicates that HDDA can improve the high-temperature oxidation resistance of FC and FCD. The weight change per unit area of the HDDA FCD is much lower than that of HDDA FC. After 72 h oxidation, the weight change per unit area of the HDDA FCD is 3.6786 mg/cm 2 , which is half of HDDA FC.   The weight change per unit area of HDDA FC/FCD follows a parabolic law in Figure 7a. Then, the oxidation kinetic curves are described by fitting the experimental data to a parabolic law ( Figure  7b): The weight change per unit area of HDDA FC/FCD follows a parabolic law in Figure 7a. Then, the oxidation kinetic curves are described by fitting the experimental data to a parabolic law (Figure 7b):

High-Temperature Oxidation Kinetic Curves
where m is the weight change per unit area of HDDA FC/FCD, Kp is a constant, and t is the oxidation time. The value of Kp can characterize the oxidation rate. The smaller the constant, the better the high-temperature oxidation resistance [20][21][22]. Kp can be calculated according to Equation (1); the Kp values for the FC and FCD are listed in Table 4. The Kp of HDDA FC is relatively high; therefore, the HDDA coating on FCD has better high-temperature oxidation resistance than that of FC. Compared to the results reported by Lin et al. [13], it can be found that the Kp value of HDDA is lower than that of hot-dip aluminizing. The main reason is that the oxidation resistance of Fe-Al alloy coating is better than that of Al alloy coating [9].

Microstructure and Phase of the HDDA Coating after Oxidation
The cross-sectional BSE microstructures of HDDA FC and FCD after oxidation are shown in Figure 8a,b. The HDDA coatings on FC/FCD are composed of two layers after oxidation. According to the EDS data in Table 5 (EDS spectra in Figure 9) and the XRD data (red and black colors were used to mark before and after oxidation, respectively) in Figure 10a,b, the outer intermetallic layer comprises the Fe 2 Al 5 phase and the inner layer comprises the FeAl phase in the HDDA on FC/FCD after oxidation. However, there is no obvious change in the thickness of the Fe 2 Al 5 coating or FeAl coating because of the low oxidation temperature and short oxidation time. After oxidation, a large amount of flaky graphite is observed in the HDDA coating on FC. The color of graphite at the interface between the HDDA coating and the FC matrix region is paler than that of the FC matrix. Figure 8c,d shows magnified images of the inner coatings on FC and FCD. Some needles can be observed in the middle of the inner coatings on the two matrixes, the distribution of which is also parallel to the interface between the outer and inner coatings. Comparison of the XRD profiles before and after oxidation shows that the number of Fe 2 Al 5 phase peaks decreases, but the number of α-Al 2 O 3 phase peaks increases. Thus, the amount of Al 2 O 3 increases after oxidation [23][24][25]. coating because of the low oxidation temperature and short oxidation time. After oxidation, a large amount of flaky graphite is observed in the HDDA coating on FC. The color of graphite at the interface between the HDDA coating and the FC matrix region is paler than that of the FC matrix. Figure 8c,d shows magnified images of the inner coatings on FC and FCD. Some needles can be observed in the middle of the inner coatings on the two matrixes, the distribution of which is also parallel to the interface between the outer and     (Figure 11c,d)). Therefore, the flaky graphite distributed throughout the HDDA coating is oxidized (2C+O2→2CO or C+O2→CO2). The flaky graphite at the interface between the HDDA coating and the matrix region is also oxidized to CO or CO2, which also explains why the color of graphite at the interface between the HDDA coating and the FC matrix region is paler than that of the FC matrix. However, only the exposed spheroidal graphite is oxidized (2C+O2→2CO or C+O2→CO2), while that inside the matrix and inner coating is not oxidized (Figure 12c,d). The occurrence of O infiltration into matrix in A region (Figure 12d) is quite special. Because the spheroidizing grade of FCD is 4, a small amount of vermicular graphite is found in FCD matrix. Exposed vermicular graphite is oxidized in region A, leading to the penetration of O past the HDDA coating into matrix. If the FCD is full of spherical graphite, the penetration of O will not occur. After oxidation of flaky graphite, many continuous oxidation channels from the surface to the matrix in the HDDA coating on FC are formed which lead to the oxidation of graphite at the interface between the HDDA coating and the matrix region and are consistent with the results reported by Lin et al. [13]. At the same time, alumina is formed around the oxidation channels in the HDDA coating, but iron oxide is formed around the oxidation channels in FC matrix. Therefore, the high-temperature oxidation resistance of the HDDA coating on FCD is much better than that on FC, which is determined by the graphite morphology.   (Figure 11c,d)). Therefore, the flaky graphite distributed throughout the HDDA coating is oxidized (2C+O 2 →2CO or C+O 2 →CO 2 ). The flaky graphite at the interface between the HDDA coating and the matrix region is also oxidized to CO or CO 2 , which also explains why the color of graphite at the interface between the HDDA coating and the FC matrix region is paler than that of the FC matrix. However, only the exposed spheroidal graphite is oxidized (2C+O 2 →2CO or C+O 2 →CO 2 ), while that inside the matrix and inner coating is not oxidized (Figure 12c,d). The occurrence of O infiltration into matrix in A region (Figure 12d) is quite special. Because the spheroidizing grade of FCD is 4, a small amount of vermicular graphite is found in FCD matrix. Exposed vermicular graphite is oxidized in region A, leading to the penetration of O past the HDDA coating into matrix. If the FCD is full of spherical graphite, the penetration of O will not occur. After oxidation of flaky graphite, many continuous oxidation channels from the surface to the matrix in the HDDA coating on FC are formed which lead to the oxidation of graphite at the interface between the HDDA coating and the matrix region and are consistent with the results reported by Lin et al. [13]. At the same time, alumina is formed around the oxidation channels in the HDDA coating, but iron oxide is formed around the oxidation channels in FC matrix. Therefore, the high-temperature oxidation resistance of the HDDA coating on FCD is much better than that on FC, which is determined by the graphite morphology.     Figure 13a,b shows the surface morphologies of the HDDA coating on FC and FCD after oxidation. The surface of the HDDA coating on FCD is dense and uniform, but the surface of HDDA FC shows peeling and warping. This is mainly due to graphite oxidation at the interface between the HDDA coating and the FC matrix region during oxidation, resulting in poor adhesion between the HDDA coating and the matrix. The XRD analysis reveals the formation of α-Al 2 O 3 on the surface of the HDDA coatings on FC and FCD, as shown in Figure 10a,b. As the HDDA coating falls off, the oxidation area increases. Thus, the value of the weight change of HDDA FC is larger than that of HDDA FCD.  Figure 13a,b shows the surface morphologies of the HDDA coating on FC and FCD after oxidation. The surface of the HDDA coating on FCD is dense and uniform, but the surface of HDDA FC shows peeling and warping. This is mainly due to graphite oxidation at the interface between the HDDA coating and the FC matrix region during oxidation, resulting in poor adhesion between the HDDA coating and the matrix. The XRD analysis reveals the formation of α-Al2O3 on the surface of the HDDA coatings on FC and FCD, as shown in Figure 10a,b. As the HDDA coating falls off, the oxidation area increases. Thus, the value of the weight change of HDDA FC is larger than that of HDDA FCD.  Figure 14 shows the average Vickers hardness of FC/FCD with and without HDDA. The hardness of FC/FCD is 220 ± 25 HV and 250 ± 24 HV, respectively, and the hardness of HDDA FC is 788 ± 32 HV. However, the hardness of HDDA FCD is higher than that of HDDA FC, which is approximately 923 ± 40 HV, as a result of the formation of pores in the outer coating of HDDA on FC.   Figure 14 shows the average Vickers hardness of FC/FCD with and without HDDA. The hardness of FC/FCD is 220 ± 25 HV and 250 ± 24 HV, respectively, and the hardness of HDDA FC is 788 ± 32 HV. However, the hardness of HDDA FCD is higher than that of HDDA FC, which is approximately 923 ± 40 HV, as a result of the formation of pores in the outer coating of HDDA on FC.  Figure 13a,b shows the surface morphologies of the HDDA coating on FC and FCD after oxidation. The surface of the HDDA coating on FCD is dense and uniform, but the surface of HDDA FC shows peeling and warping. This is mainly due to graphite oxidation at the interface between the HDDA coating and the FC matrix region during oxidation, resulting in poor adhesion between the HDDA coating and the matrix. The XRD analysis reveals the formation of α-Al2O3 on the surface of the HDDA coatings on FC and FCD, as shown in Figure 10a,b. As the HDDA coating falls off, the oxidation area increases. Thus, the value of the weight change of HDDA FC is larger than that of HDDA FCD.  Figure 14 shows the average Vickers hardness of FC/FCD with and without HDDA. The hardness of FC/FCD is 220 ± 25 HV and 250 ± 24 HV, respectively, and the hardness of HDDA FC is 788 ± 32 HV. However, the hardness of HDDA FCD is higher than that of HDDA FC, which is approximately 923 ± 40 HV, as a result of the formation of pores in the outer coating of HDDA on FC.  This phenomenon can be explained by the pores formation due to flaky graphite oxidation during the diffusion process, resulting in poor internal adhesion of the Fe 2 Al 5 intermetallic coating. Therefore, some particles will fall off during the wear process, resulting in greater fluctuation of the friction coefficient of HDDA FC. The average abrasion losses of FC/FCD with and without HDDA are shown in Figure 15b: 0.8108 mm 3 , 0.5926 mm 3 , 0.2732 mm 3 , and 0.3613 mm 3 for HDDA FC, FC, HDDA FCD, and FCD, respectively. The lower the average abrasion loss, the better the wear resistance is [26,27]. Thus, the wear resistance of FCD can be improved by HDDA, which has no obvious effect on the wear resistance of FC. It should be noted that the friction coefficient increased after HDDA, which worth being studied further in the future. to flaky graphite oxidation during the diffusion process, resulting in poor internal adhesion of the Fe2Al5 intermetallic coating. Therefore, some particles will fall off during the wear process, resulting in greater fluctuation of the friction coefficient of HDDA FC. The average abrasion losses of FC/FCD with and without HDDA are shown in Figure 15b: 0.8108 mm 3 , 0.5926 mm 3 , 0.2732 mm 3 , and 0.3613 mm 3 for HDDA FC, FC, HDDA FCD, and FCD, respectively. The lower the average abrasion loss, the better the wear resistance is [26,27]. Thus, the wear resistance of FCD can be improved by HDDA, which has no obvious effect on the wear resistance of FC. It should be noted that the friction coefficient increased after HDDA, which worth being studied further in the future. The 3D morphology of the wear track profile in Figure 16a,b shows the depth of the wear tracks for the HDDA coatings on FC and FCD. The depth of the grinding mark of HDDA FC is clearly greater than that of HDDA FCD in the 3D wear figure. The average wear depth and width are shown in Table 6, and the values are consistent with the 3D profile. It can be concluded that the HDDA coating on FCD is more stable to friction and wear than that of the HDDA FC.

Conclusions
The graphite morphology did not affect the phase composition of the HDDA coating on FC/FCD, but it determined the microstructure and properties of the coating. The HDDA coatings on FC/FCD consisted of an outer Fe2Al5 topcoat and an inner FeAl layer. A large amount of flaky graphite was found throughout the HDDA coating on FC, which featured some pores. However, spheroidal graphite was also embedded in the HDDA coating, resulting in a dense and uniform morphology. The flaky graphite provides a channel for the penetration of O past the HDDA coating into matrix， The 3D morphology of the wear track profile in Figure 16a,b shows the depth of the wear tracks for the HDDA coatings on FC and FCD. The depth of the grinding mark of HDDA FC is clearly greater than that of HDDA FCD in the 3D wear figure. The average wear depth and width are shown in Table 6, and the values are consistent with the 3D profile. It can be concluded that the HDDA coating on FCD is more stable to friction and wear than that of the HDDA FC. to flaky graphite oxidation during the diffusion process, resulting in poor internal adhesion of the Fe2Al5 intermetallic coating. Therefore, some particles will fall off during the wear process, resulting in greater fluctuation of the friction coefficient of HDDA FC. The average abrasion losses of FC/FCD with and without HDDA are shown in Figure 15b: 0.8108 mm 3 , 0.5926 mm 3 , 0.2732 mm 3 , and 0.3613 mm 3 for HDDA FC, FC, HDDA FCD, and FCD, respectively. The lower the average abrasion loss, the better the wear resistance is [26,27]. Thus, the wear resistance of FCD can be improved by HDDA, which has no obvious effect on the wear resistance of FC. It should be noted that the friction coefficient increased after HDDA, which worth being studied further in the future. The 3D morphology of the wear track profile in Figure 16a,b shows the depth of the wear tracks for the HDDA coatings on FC and FCD. The depth of the grinding mark of HDDA FC is clearly greater than that of HDDA FCD in the 3D wear figure. The average wear depth and width are shown in Table 6, and the values are consistent with the 3D profile. It can be concluded that the HDDA coating on FCD is more stable to friction and wear than that of the HDDA FC.

Conclusions
The graphite morphology did not affect the phase composition of the HDDA coating on FC/FCD, but it determined the microstructure and properties of the coating. The HDDA coatings on FC/FCD consisted of an outer Fe2Al5 topcoat and an inner FeAl layer. A large amount of flaky graphite was found throughout the HDDA coating on FC, which featured some pores. However, spheroidal graphite was also embedded in the HDDA coating, resulting in a dense and uniform morphology. The flaky graphite provides a channel for the penetration of O past the HDDA coating into matrix，

Conclusions
The graphite morphology did not affect the phase composition of the HDDA coating on FC/FCD, but it determined the microstructure and properties of the coating. The HDDA coatings on FC/FCD consisted of an outer Fe 2 Al 5 topcoat and an inner FeAl layer. A large amount of flaky graphite was found throughout the HDDA coating on FC, which featured some pores. However, spheroidal graphite was also embedded in the HDDA coating, resulting in a dense and uniform morphology. The flaky graphite provides a channel for the penetration of O past the HDDA coating into matrix, but the spherical graphite can well prevent the penetration of O. Therefore, the high temperature oxidation resistance and wear resistance of HDDA FCD are about three times that of HDDA FC.