arose when electrodes were in contact. The electrospark coatings were formed due to the multiple overlaps of single-discharge spots.

The interelectrode voltage during the pulses was maintained at 40 V. The discharge current amplitude was 100 A, while the frequencies of pulses were 100 and 1000 Hz. The pulse-on duration was 100 μs, the frequency of the anode vibro-excitor was 100 Hz. The total deposition time for each sample was 5 min in air. After every 60 s the deposition process was interrupted and the cathode and

Table 2. Properties of sintered WC-Co-C electrodes.

anode were weighed separately on an electronic balance Vibra HTR-220CE with accuracy up to 10−4 g. The microstructure of samples was analysed with the aid of an optical microscope. The microstructure and chemical composition of the coatings were analysed using an optical microscope and an EVO 40HV scanning electron microscope (SEM) (Carl Zeiss, Germany) with an INCA Energy 350 energy-dispersion spectrometer (Oxford Instruments, UK). The phase composition of the produced coatings was examined by a DRON-7 X-ray diffractometer (Burevestnik, Russia) equipped with a Cu-Ka radiation source in Bragg-Brentano geometry. The microhardness was measured by the Vickers method with a PMT-3M tester (Russia) under a load of 50 N. The abrasive wear resistance of the electrospark coatings was measured by a Calotest friction machine (CSM Instruments, Switzerland) using the “ball-plate” scheme [11]. A ball with a diameter of 30 mm was rotated at a linear velocity of 0.27 m/s. Aluminium oxide powder in solar oil was employed as an abrasive material.

3. Results and Discussion

3.1. Properties of Electrodes

The composition of samples was examined by an X-ray diffractometer DRON-7 (Russia) with Cu-Ka radiation in Bragg-Brentano geometry. XRD analysis of the prepared electrodes showed that their phase composition was highly dependent on the carbon content (Figure 1). Peaks of tungsten carbide (WC) and tungsten semicarbide (W2C) were observed in the spectra of the 1.5A, 2.5A, and 3.5A electrodes, in which carbon was deficient. The composition of the 5.5A electrode was close to the standard hard alloy WC-10%Co. For 4.5A and 8A samples, only the WC carbide was discovered. In the spectra of the 8А and 10A, electrodes that contained more carbon, a carbon peak appeared besides reflections of tungsten carbide.

Figure 1. XRD patterns of synthesized electrode materials.

3.2. Mass Transfer

It is typical of electrospark alloying that the masses of both electrodes vary as a consequence of the erosion and the preemptive transfer of metal from the anode onto the cathode. The amount of anode material transferred to the substrate is an important characteristic because it determines the thickness of the deposited coating [1,12]. Our investigations showed that the kinetic curves of the change in electrode mass depended strongly on the carbon concentration of the electrode materials (Figure 2). The maximum cathode gain was 28.6 mg for the 1.5C sample. The weight gain of the cathode processed with electrode no. 10A was the least and equalled 9.2 mg. In addition, it was established that the anode erosion rate was correlated with the strength of the electrode material (Figure 3). With an increase in the anode strength from

Figure 2. Mass changes of cathodes and anodes with different carbon concentrations.

Figure 3. Anode erosion rate as a function of its strength.

0.06 to 1.5 GPa, the erosion rate reduced more than 5- fold, from 15.9 to 2.8 mg/min. This is because electrodes with low strength are less resistant to thermo-mechanical loads during the discharge process. The greatest strength of 1.477 GPa and the lowest erosion rate of 2.8 mg/min were attained by the electrode corresponding to the standard WC-10%Co with a carbon concentration of 5.5 wt%.

3.3. Structure and Composition of Coatings

The electrospark treatment of steel 1035 by applying the WC-Co-C electrodes was carried out during 5 min in air with a pulse length of 100 μs. The investigations showed that the compositions of the obtained coatings were different (Figure 4). When anodes with lower carbon contents (1.5A, 2.5A, 3.5A) and a pulse frequency of 100 Hz were employed, the WC carbide was not detected in the deposited layers, but semicarbide W2C was observed, which is indicative of the occurrence of decarburization upon interaction of WC with the iron substrate, which was also observed for electrospark coatings deposition [5] and HVOF spraying [13,14]. On the other hand, when the electrodes with excess carbon (8А, 10A) were used, the tungsten carbide WC dominated in the electrospark coatings. Thus, the addition of carbon into the electrode WC-10%Co materials allowed the amount of WC phase in deposited layers to increase. The decarburization of hard alloy was intensive at a higher discharge frequency of 1 kHz (Figure 5). The 5.5C coating created at this frequency consisted almost completely of W2C together with small amounts of WC and iron in contrast to the same coating deposited at 100 Hz. When the 10A anode with higher carbon content was used, the WC carbide dominated over semicarbide W2C and iron in the coating composition but less so than at the frequency of 100 Hz.

Figure 4. XRD patterns of coatings obtained by the electrospark treatment using electrodes with various carbon concentrations at a frequency of 100 Hz.

Figure 5. XRD patterns of the coatings obtained by the electrospark treatment with electrodes 5.5A and 10A at a frequency of 1 kHz.

Figure 6 shows cross-sectional images of surface layers of steel 1035 after electrospark alloying with different anode materials. The thickness of the obtained coatings was 33 - 45 µm (Table 3). The 1.5C, 2.5C, and 3.5C coatings were considerably fragmented due to the presence of brittle W2C phase that failed under thermo-mechanical loads during discharges. The structure of surface layers deposited by the application of anodes with higher carbon contents was more uniform although there were some micropores. In regions of steel 35 adjoining the interface between the coating and the substrate, a pearlite structure formed because of the short duration of quenching.

SEM images of the surface and cross-sections of the obtained layers show the presence of grains whose elemental composition corresponds to tungsten carbide (WC). Moreover, the amount of these grains is much larger in the 10C coating than in the 5.5С one (Figure 7).

EDS data analysis showed that 20 - 37 at.% of iron is present in the obtained coating (Figures 7(c)-(d), Table 3). Its concentration remains practically constant over the cross-section of the layer. The concentration of carbon also does not change along the cross-section of the layer. However, it was established that with increasing carbon content in the electrode, its concentration in the coating increased, since the carbon concentration of the coating of the 10C sample ranged from 30 to 40 at.%, while that obtained using the standard electrode (5.5C) was 26 - 31 at.%. It is remarkable that on the substrate areas adjacent to the interface (Figures 7(c)-(d), Table 3; points 5,6), the carbon concentration was higher than in the volume of the steel substrates. This may be explained by the diffusion of carbon from the coating to the top layers of the substrate. Thus, the addition of carbon into the electrode materials can increase its content in the coating and prevent decarburization of tungsten carbide due to saturation of the iron present in the coating by additional carbon.

3.4. Mechanical Properties of Coatings

One of the advantages of hard alloy coatings is their high wear resistance [15-17] and therefore this characteristic was determined for the obtained electrospark coatings deposited during 5 min at a frequency of 100 Hz. The wear testing showed that the wear resistance of all cathode surfaces modified by the electrospark treatment with the use WC-Co-C electrodes increased by a factor of four or more in comparison with the steel substrate. Figure 8 shows that 8C and 10C coatings have the highest wear resistance. The wear resistance of the 10C coating obtained at a higher discharge frequency of 1 kHz was seven times higher than that of a conventional 5.5C sample.

Figure 6. Cross-sectional views of electrospark coatings: (a) 1.5C; (b) 5.5C; (c) 8C.

Table 3. Elemental composition (at.%) according to EDXS data.

Figure 7. SEM images of the surface (a), (b) and cross-section (c), (d) of the coatings deposited with electrodes containing 5.5% (a), (c) and 10% (b), (d) carbon.

Table 4 shows that the average thickness of the coatings varied between 34 to 44 microns. Despite the fact that the gain in weight of the cathodes with 1.5C - 4.5C was higher than the 5.5C - 10C to almost the same thickness. This can be explained by the higher erosion of the substrate for samples with 5.5C - 10C. The average microhardness of the created coatings is presented in Table 4. It can be seen that modified surface layers have higher microhardness than steel 1035 (2.18 GPa) [18,19]. With increasing carbon content in the anode materials, the microhardness of electrospark coatings deposited with their application decreases. This is explained by the fact that the W2C is a harder phase as compared to WC but is brittle [20].

Figure 8. Wear rate of coatings in comparison with steel 35.

Table 4. Average thickness and microhardness of electrospark coatings.

4. Conclusions

1) Electrode materials with different carbon concentrations were prepared on the basis of WC-10%Co. Electrospark coatings deposited with electrodes on the basis of the WC-10%Co with different carbon concentrations onto medium-carbon steel 1035 were found to exhibit a higher WC concentration compared to those deposited with conventional WC-Co electrodes. An increase in carbon concentration in WC-Co-C electrode materials can reduce the decarburization of WC in electrospark coatings.

2) An increase in carbon concentration in WC-Co-C electrode materials can increased the wear resistance of WC-Co electrospark coatings. The best wear resistance of coatings is obtained with a carbon concentration of 8 - 10 wt% in the electrodes.


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