Introduction. In modern mechanical engineering, surface hardening of parts is a widely used technique [1]. Known technologies make it possible to obtain products with different properties and structures [2] by changing the properties and structure of the surface layer [3]. Special attention should be paid to chemical and thermal hardening methods. They are characterized by simplicity [4], provide high-quality hardened surfaces [5], as well as a smooth change in structure and properties from coating to coated material [6]. The technology of diffusion alloying from the medium of low-melting liquid metal solutions (DALMMS) refers to the technologies of chemical and thermal treatment (CCTT) and is promising from the point of view of obtaining functional coatings [6]. This technology is used to form coatings based on Cr, Ti, W, Mo, Ni, Cu, etc. on the surface of products made of steels [6], hard alloys [7], and cast iron [8].

Chromium is one of the elements that is often used as a basis for functional coatings [9]. These coatings increase wear resistance of parts [10] and corrosion resistance in aggressive environments [11]. Chrome coatings can also improve resistance to simultaneous complex effects of mechanical and corrosive wear [12]. The high resistance to wear and corrosion is due to the fact that the coatings are based on carbides [13]. During the formation of these carbides, carbon diffuses from the coated material. As a result, the carbon content in the alloy under the coating decreases, leading to the formation of decarbonization zones. This causes the carbide layer to press onto the coated part during operation [14]. To counteract the effect of decarburization and further harden the coated material, complex chemical and thermal treatment (CCTT) can be employed. It means the pre-carburization and diffusion alloying of samples with chromium in the medium of low-melting liquid metal solutions [15].

The aim of this research was to analyze the effect of pre-carburization on the formation of chromium-based diffusion coatings and the structure of the coated sample.

Materials and Methods. CCTT and DALMMS were performed on cylindrical samples with a diameter of 20 mm and a length of 30 mm. The samples were made of St3 and 40X steel (Table 1).

Chrome coatings were obtained through the process of diffusion alloying of samples in low-melting liquid metal solutions. To do this, we used the DALMMS setup [16]. The reaction transport medium was a PbLi eutectic melt, into which 10% chromium powder was added. The coating was applied by immersing and then isothermally exposing the samples in the melt at 1050°C for 8 hours, with argon filling the space above the melt. This process also involved solid-phase diffusion, leading to the formation of solid solutions and chemical compounds.

Prior to the start of DALMMS, in order to saturate the surface layers of steels with carbon, vacuum carburization was performed in a propane-butane mixture at a temperature of 950°C for 8 hours.

The structure of the coated material and the thickness of the coating were studied using a NU-2E universal optical microscope (Carl Zeiss Jena). The microhardness of the samples after DALMMS and CCTT was studied on a Dura Scan Falcon 500 microhardness tester. Electron microprobe analysis was performed on a Tescan Lyra 3 scanning electron microscope with the Oxford Ultim MAX PCMA system. An X-ray diffractometer Bruker D8 Advance Eco (Bruker AXS GmbH) with a θ-θ vertical goniometer was used for X-ray phase analysis (XPA). The samples were etched in a 4% alcohol solution of HNO3.

Results. Figure 1 shows micrographs of St3 steel samples after DALMMS and CCTT.

Thus, pre-carburization affected both the steel and coating structure after DALMMS. Without pre-carburization, carbon diffused into the area under the coating, forming a pearlitic layer and a decarbonized ferritic layer in which there were no pearlitic grains. If pre-carburization was performed, the structure of the coated material changed. After CCTT, there was no decarbonized ferritic sublayer in it, even when low-carbon St3 steel was saturated. The structure of the material was perlite with ferrite inclusions (Fig. 1b).

Several zones could be distinguished that formed the surface layers of the material after CCTT:

Figure 2 shows the structure of a 40X steel sample after CCTT.

In case of DALMMS without pre-carburization, a zone of lamellar perlite alloyed with chromium was formed under the coating, followed by a soft ferritic layer. There was no decarbonized layer in the pretreated samples. Without carburization, a coating with a thickness of 12 µm was formed on the St3 steel sample; with carburization it was 22 µm. Thus, pre-carburization helped to increase the coating thickness by 1.83 times. There was a physical explanation for this result. Pre-carburization increased the intensity of carbon diffusion from the sample to the adsorbed chromium. Carbon heterodiffusion was recorded under the influence of high temperatures characteristic of DALMMS. This helped to equalize the carbon content and eliminate decarbonized zones that could occur as a result of the formation of carbides. Figure 3 shows micrographs of 40X steel after DALMMS and CCTT. On the sample after CCTT, the perlite structure was thinner, and there was no decarbonized zone.

Carburization did not significantly affect the chemical and phase composition. In both cases, the chromium content on the surface was 90% (wt.). However, the depth of chromium diffusion in the sample without carburization was 18 µm. In the sample with pre-carburization it was 34 µm, that is, twice as much. The results of electron microprobe analysis of the samples are shown in Figure 4.

Phase composition of the coatings was represented by chromium carbides M23C6 and M7C3. In the sample without pre-carburization, there was a slight iron content in chromium carbide M23C6 (Fig. 5).

Pre-carburization provided a significant increase in the depth of the hardened layer (Fig. 6).

According to Figure 6, on samples without pre-carburization, the microhardness index of the coating after DALMMS for St3 steel was 1400 HV0,02, 40Х — 1650 HV0,02. After CCTT, the microhardness of the St3 steel coating was 1500 HV0,02, 40Х — 1800 HV0,0. However, at a depth of 10 µm, the microhardness was 160 HV0,02. This was lower than the microhardness of the coated material in both cases (i.e. for St3 and 40X samples). After CCTT, the microhardness distribution had a different character:

Discussion and Conclusion. Thus, under the conditions considered, the main effect of carburization was manifested in the intensification of coating growth and the exclusion of the formation of a soft ferritic layer between the coating and the coated material. The composition of the coating and the chromium content did not depend on carburization. In any case, the coatings consisted of chromium carbides such as M23C6 and M7C3, the chromium content on the surface reached 90%.

CCTT affected the structure of the layer between the coating and the base material. In case of DALMMS, the layer under the coating had a pearlitic structure, turning into a ferritic one and further into the structure of the coated material. Pre-carburization made the transition zone more uniform. Here, a pearlitic structure was formed with a gradual change in chromium concentration — from 10% at the boundary of the coating and the pearlitic zone to 0.3% at a depth of 35 µm.

Thus, the positive results of pre-carburization have been proven. Firstly, the carbon content in the surface layers of the product increased, and this made it possible to intensify carburization.

Secondly, it became possible to obtain a carbon-saturated layer between the coating and the base material, which also strengthened the structure of the coated material. Therefore, it can be argued that pre-carburization is promising in terms of expanding the scope of application of parts with diffusion coatings based on chromium carbide. It eliminates the penetration of the layer under the coating and its subsequent destruction. The parts after CCTT are capable of operating at high contact stresses without chipping the functional layer.

Thirdly, the formation of a diffusion coating is accelerated. In addition, it will be thicker. As part of this study, the indicator was 1.83. The coating obtained after carburization was that much thicker (compared with the technology without pre- carburization). This indicates the significant role of carbon in the mechanism of coating creation.