A Study of the Phase-Structural Engineering Possibilities of Coatings on D16 Alloy During Micro-Arc Oxidation in Electrolytes of Different Types

The effect of electrolysis conditions with different electrolyte compositions on the growth kinetics, phase-structural state, and hardness of coatings obtained by microarc oxidation (MAO) on the D16 aluminum alloy (base – aluminum, main impurity Cu) was studied.<br><br>An analysis of the results obtained showed that the choice of the type of electrolyte and the conditions for the MAO process makes it possible to vary the growth kinetics and phase-structural state of the coating on the D16 aluminum alloy within a wide range. For all types of electrolytes, with an increase in the content of KOH, Na2SiO3, or KOH+Na2SiO3, the growth rate of MAO coatings increases.<br><br>It was found that in MAO coatings obtained in an alkaline (KOH) electrolyte, a two-phase (γ−Al2O3 and α−Al2O3 phases) crystalline state is formed. An increase in the KOH concentration leads to an increase in the relative content of the α–Al2O3 phase (corundum). During the formation in a silicate electrolyte, the phase composition of MAO coatings with an increase in the content of liquid glass (Na2SiO3) changes from a mixture of the γ−Al2O3 phase and mullite (3Al2O3∙2SіO2) to an X-ray amorphous phase. The use of a complex electrolyte leads to a two-phase state of the coating with a large (compared to an alkaline electrolyte) shift of the γ−Al2O3→α−Al2O3 transformation towards the formation of the α−Al2O3 phase. It was determined that the value of hardness correlates with the content of the α−Al2O3 phase in the MAO coating, reaching the maximum value of 1620 kg/mm2 at the highest content (about 80 vol. %) of the α−Al2O3 phase.<br><br>Two types of dependences of the coating thickness on the amount of electricity passed were revealed. For the amount of passed electricity 10–50 A-h/dm2, the thickness dependence is determined as 4.2 μm/(A-h/dm2), which suggests the basic mechanism of electrochemical oxidation during the formation of a coating. For the amount of electricity transmitted 50–120 A-hour/dm2, the thickness dependence is determined by a much smaller value of 1.1 μm/(A-hour/dm2). This suggests a transition to a different mechanism of coating formation − the formation of a coating with the participation of electrolysis components.


Introduction
Coatings are the basis of most modern technologies in mechanical engineering, aircraft construction and medical technology [1,2]. The most promising directions in the field of creating multifunctional coatings are multi-element [3,4], multilayer [5,6] and hybrid (formed from a base material with a partial thickness increment [7,8]) coatings. In recent years, the method of structural engineering of coatings has been effectively used to form coatings with desired properties [9,10].
The method of structural engineering of coatings (i. e., determination of regularities of structural states depending on the parameters of obtaining coatings) has gained especially great importance due to the use of highly nonequilibrium methods of their formation from plasma [11,12].
(Al, Ti, Mg, Nb, Zr, etc.), which transforms surface layers into oxide ceramic coatings [13,14]. This process was originally called plasma electrolytic oxidation (PEO) [15,16], and somewhat later -anodic spark deposition (ASD) [17]. However, the most frequently used name recently in describing this process is microarc oxidation (MAO) [18,19]. As a result of the MAO process, coatings with a thickness of 100-300 µm are formed on the surface with a unique combination of physical and mechanical properties (high hardness, wear resistance, heat resistance, heat strength, corrosion resistance, etc.) [20,21].
Therefore, at present, the industrial implementation of this technology is very promising, and the development of the method of structural engineering to achieve the required properties in coatings of this type is an urgent and demanded task.

Literature review and problem statement
As shown in [22,23], there is a fundamental difference between anodizing and microarc oxidation. Unlike anodizing, where oxidation does not occur by continuous transfer of ions through the electrolyte (in a thin oxide layer), in microarc oxidation, oxidation occurs due to the combination of metal and oxygen atoms (or ions) in the discharge plasma. This mechanism facilitates the production of thicker oxide layers and often results in a harder and larger crystallite structure. The main reason for this is that the discharges generate a large amount of heat, which promotes crystallization in the surrounding oxide material [24,25]. In this case, during the MAO treatment, there is no significant increase in the substrate temperature [26,27].
A specific feature of the MAO process is the use of valve materials on which oxide films (formed electrochemically) have unipolar or asymmetric conductivity in the metal -oxide -electrolyte (MOE) system [28,29]. In this case, the positive potential on the metal (on which the anodic oxide film is formed) corresponds to the blocking or reverse direction, i. e., the system works similarly to a semiconductor valve.
Thus, MAO is simultaneously characterized by the features of two different groups of modification methods: coating deposition (with an increment in thickness) and changes in the structure and properties of the surface and near-surface layers (without an increment in thickness) [30,31].
Using this method, the highest properties have now been obtained on aluminum alloys [32,33]. This is associated with the possibility of the formation of a highly hard α-Al 2 O 3 phase during the MAO process [34,35].
However, the mechanism of the formation of this phase, due to the complexity and heterogeneity of the MAO process, cannot yet be theoretically predicted. Therefore, to determine the patterns and mechanisms of the formation of the phase-structural state in the MAO process, empirical data are currently used for different technological conditions [36,37]. In this case, as a rule, the phase composition of the coatings changes over the MAO layer thickness [38,39]. During MAO processing of alloys based on aluminum, it was found that high-temperature modifications of aluminum oxide are in its inner layers. Towards the outer surface of the modified layer, the amount of low-temperature modifications of aluminum oxide increases. It is assumed that the latter is associated with the conditions of electrolysis at the initial stages of anode-spark treatment, since the temperature of the metal sections adjacent to the discharge craters is only 400-500 °C [40].
Also, a very important factor in the MAO treatment is the type and number of impurity atoms. Usually, metals with a high free energy of oxide formation are used as impurity atoms [41]. However, in many cases, aluminum alloys with other alloying elements are used to achieve the required performance characteristics. In particular, the main alloying element of the widely used D16 alloy (and its analogs) is copper, which has low oxidation energy. The effect of such a combination of elements can lead to specific features of the kinetics of the growth of coatings and their phase-structural formation [42,43]. For this type of alloy (D16), it is known to use aqueous solutions based on sodium hydroxide (NaOH) as electrolytes [44]. Studies of MAO coatings with an alkaline constituent of NaOH electrolyte have shown that even in a complex electrolyte (NaOH+Na 2 SiO 3 ), their growth kinetics is relatively low (the growth rate at a thickness of more than 100 µm does not exceed 0.5 µm/min) [44]. The proportion of the hardest α-Al 2 O 3 phase does not exceed 70 vol. %. Since the stability of the electrolyte requires an alkaline medium with a high pH (hydrogen index), an increase in the kinetics of coating growth can be expected when using potassium hydroxide (with a higher pH=13) as an alkaline electrolyte component [41].
Therefore, for electrolysis in alkaline electrolytes, it is important, both from a scientific and a practical point of view, to determine the regularities necessary for the phase-structural engineering of MAO coatings. As follows from [41], such regularities should be based on the influence of the type and composition of electrolytes and treatment modes on the kinetics of MAO coatings growth, the quantitative ratio of different phases and their structural states in them.

The aim and objectives of the study
The aim of the study was to examine the effect of the type (KOH, Na 2 SiO 3 and KOH+Na 2 SiO 3 solutions) and composition of the electrolyte on the growth kinetics of MAO coatings on the D16 alloy, the formation of their phase-structural state, and the effect of the phase composition on hardness.
To achieve this goal, the following objectives were set: -to study the effect of the compositions of alkaline (KOH solutions) and silicate (Na 2 SiO 3 solutions) electrolytes on the growth kinetics and phase composition of MAO coatings; -to determine the growth kinetics of MAO coatings formed in a complex (KOH+Na 2 SiO 3 solutions) electrolyte; -to study the effect of the complex (KOH+Na 2 SiO 3 solutions) electrolyte on the formation of the structural-phase state and the hardness of MAO coatings, as well as the electrolysis conditions (the amount of electricity passed) in the electrolyte of this type on the thickness of the formed coatings. Since the MAO process does not require specialized surface treatment (for example, etching or degreasing), the preliminary surface treatment before MAO treatment was only grinding of surface irregularities on abrasive paper.
Microarc oxidation was carried out in a 100-liter bath. During the MAO process, cooling and bubbling of the electrolyte were provided. The average voltage was 380 V. The initial current density was 20 A/dm 2 , the duration of treatment was varied.
A typical microstructure of the lateral section of the near-surface layer of the alloy after MAO treatment is shown in Fig. 1.
One can see the formation, which is standard for the MAO process of aluminum alloys, in addition to the hard base layer of a technological surface layer with low hardness [44]. The technological surface layer (usually with a thickness of 30-40 % of the base layer) with low hardness after the MAO process was removed by the standard grinding method [44].
Therefore, the results obtained in this work refer to the main (base) coating layer.
The determination of the phase composition of MAO coatings was carried out according to the results of X-ray phase analysis. The studies were carried out on a DRON-3 setup (Burevesnik, Russia) in monochromatic K α -Cu radiation. Diffraction spectra were recorded using the Bragg-Brentano reflection scheme [45]. The survey was carried out both in continuous and pointwise mode with a step of 2θ=0.1°. The maximum error in determining the content of structural crystalline components (with a detectability of 10 vol. %) does not exceed ±0.7 %. The minimum detectability of structural components is about 1 vol. %. This detection accuracy was determined by comparing the reference lines of the phases with the base mixtures.
For quantitative phase analysis, the method of reference mixtures was used [46]. For this, calibration graphs of the dependence of the intensities of the comparison lines on the mixture composition were constructed. Α-Al 2 O 3 (ASTM Card File 10-173), γ-Al 2 O 3 (ASTM Card File 10-425) and mullite (3Al 2 O 3 •2SiO 2 , ASTM Card File 15-776) were used as the basic components of the coating composition. If peaks from the aluminum substrate appeared in the diffraction spectra, they were not taken into account when calculating the coating composition.
The coating thickness was determined on a VT-10 NTs vortex thickness gauge (Kontrolpribor, Russia). The error in measuring the coating thickness is no more than 5 % at the smallest coating thickness (about 10 microns). With a larger coating thickness, the accuracy of determining the thickness increases (for example, at a thickness of 50 µm, the measurement error is no more than 2 %).
The thickness of the layers on the VT-10 NTs device was determined sequentially: first, as complete (base and technological layer), and after grinding the technological layer, the thickness of the base layer was determined.
To determine the amount of electricity Q passed through, the product of current and processing time was used.

1. Growth kinetics and phase composition of MAO coatings during oxidation in alkaline and silicate electrolytes
An alkaline electrolyte is a solution of caustic potassium (KOH) in distilled water, and a silicate electrolyte is an aqueous solution of sodium (Na 2 SiO 3 ) or potassium (K 2 SiO 3 ) water glass.
The introduction of alkali into the electrolyte significantly reduces the outer technological layer. In this case, one of the main factors for the effective use of alkaline electrolyte is the growth kinetics of the coating. Fig. 2 shows the dependences of the thickness of the coatings on the D16 alloy for different KOH contents in the alkaline electrolyte.
It is seen that with an increase in the KOH content, the growth rate of the coating on the D16 alloy increases. Based on the obtained dependences, the kinetic factor (coating growth rate V ) varies from V 1 g/L-KOH = =0.33 µm/min and V 2 g/L-KOH =0.83 µm/min to V 5g/L-KOH =1.33 µm/min. Thus, with an increase in the KOH content in the electrolyte from 1 g/L KOH to 5 g/L KOH, the growth rate of the coating increases by more than 4 times.
However, the use of the 5 g/L KOH content is apparently the highest for the process with the formation of microarc discharges. As was found experimentally, at a higher KOH content in the electrolyte, the oxidation process in the microarc discharge mode does not occur, which does not allow the MAO coating to grow (accordingly, at a higher KOH content, there is no possibility of plotting kinetic  Fig. 2). The reason for this may be the formation of a relatively thick dielectric layer on the growth surface, for which the breakdown voltage significantly exceeds the characteristics in a microarc discharge. The regularities of the formation of the phase composition and structure that are formed in MAO coatings are the basis for the scientific substantiation and use of the method of phase-structural engineering. Fig. 3 shows a typical X-ray diffraction spectrum of an MAO coating on the D16 alloy in an alkaline electrolyte.
It is seen that the main component of the coating is γ-Al 2 O 3 . Diffraction peaks of the base material (aluminum) are detected by the presence of sample anchorage points, at which oxidation did not occur. In addition to γ-Al 2 O 3 , diffraction peaks from the α-Al 2 O 3 phase (corundum) are revealed in the diffraction spectra. This indicates the presence of crystallites of this phase in the coating.
The dependence of the change in the phase composition on the KOH content in the electrolyte is shown in Fig. 4, a.
As can be seen from the data obtained, the coating formation process begins with the formation of the γ-Al 2 O 3 phase. An increase in the processing time leads to the appearance of α-Al 2 O 3 as a result of the thermodynamically favorable polymorphic transformation γ-Al 2 O 3 →α-Al 2 O 3 [47]. It can be seen that with an increase in the KOH content, the ratio of the volumetric content of γ-Al 2 O 3 and α-Al 2 O 3 phases changes towards a relative increase in the α-Al 2 O 3 phase. This effect is explained by an increase in the relative thickness of the dielectric layer with an increase in the KOH content in the electrolyte. With an increase in the thickness of such a layer, the power of microarc discharges (and, accordingly, the temperature of the microarc process) increases, which stimulates an increase in the completeness of the polymorphic transformation γ-Al 2 O 3 →α-Al 2 O 3 .
An increase in the time of microarc oxidation leads to a further change in the α-Al 2 O 3 /γ-Al 2 O 3 ratio. Fig. 5 shows the dependences of the phase ratio with increased duration of micro-arc oxidation by 3 times (up to 180 minutes). Fig. 5 shows that an increase in the duration of the MAO process over 60 minutes leads to a significant increase in the relative content of the hardest α-Al 2 O 3 phase in the MAO coating. In this case, as can be seen from Fig. 2, the thickness of such coatings reaches 170 µm.
The second, promising from the point of view of technology and ecology of obtaining a coating, is an aqueous solution of sodium or potassium liquid glass [33].
To study the possibilities of phase-structural engineering of MAO coatings on the D16 alloy, we used sodium liquid glass Na 2 SiO 3 (GOST 13078-81). Thus, a silicate electrolyte was obtained, the concentration of Na 2 SiO 3 in which varied in the range of 10-50 g/L.  The growth kinetics of the coating, determined from its thickness, is shown in Fig. 6. It can be seen that for the composition of the silicate electrolyte with 10 g/L Na 2 SiO 3 , the growth rate V 10 g/L-Na2SiO3 =1.08 µm/min. An increase in the content of water glass in the electrolyte to 25 g/L Na 2 SiO 3 leads to a significant increase in the growth rate of the coating up to V 25 g/L-Na2SiO3 =2.25 µm/min. The highest growth rate of the coating (V 50 g/L-Na2SiO3 =8 µm/min) was achieved when the electrolyte contained 50 g/L Na 2 SiO 3 (Fig. 6).
It can also be noted that in order to achieve a thickness of 100 µm (used for comparison), depending on the amount of liquid glass, there is a significant change in the time of the MAO process. With a relatively small content of 10 g/L Na 2 SiO 3 (Fig. 6, dependence 1), to achieve a working thickness of 100 µm, it is necessary to carry out the MAO process for 120 minutes. In an electrolyte containing 25 g/L Na 2 SiO 3 , 47 minutes of the MAO process is enough to reach a thickness of 100 µm. Note that at the highest Na 2 SiO 3 content of 50 g/L, it takes only 15 minutes to achieve an MAO coating thickness of 100 µm.
As seen from Fig. 7, the typical form of the X-ray diffraction patterns is characterized by the formation of mainly mullite (3Al 2 O 3 •2SiO 2 ), γ-Al 2 O 3 , and an amorphous-like phase. An increase in the duration of the pro-cess for a silicate electrolyte mainly leads to an increase in the content of the X-ray amorphous phase (Fig. 4, b). Thus, in the silicate electrolyte there is a significant decrease in the size of the regions of formation and the transition from the crystalline structure of the coating to nanodispersed (X-ray amorphous).
The generalized dependences of the change in the phase composition on the content of water glass are shown in Fig. 4, b. It can be seen that only at a relatively low content of liquid glass (10 g/L Na 2 SiO 3 ), the two-phase state from γ-Al 2 O 3 and 3Al 2 O 3 •2SiO 2 (mullite) phases is achieved. Moreover, as follows from Fig. 6, the deposition rate of such a coating is V 10 g/L-Na2SiO3 =1.08 µm/min. If compared with the data in Fig. 2, 4, а for an alkaline electrolyte KOH, at its highest content of 5 g/L, the two-phase state is also formed, but at a higher growth rate V 5g/L-KOH = =1.33 µm/min. However, not only the growth rate is higher, but most importantly, the second phase is not 3Al 2 O 3 •2SiO 2 (mullite) (as in silicate electrolyte), but the hardest α-Al 2 O 3 (corundum).

2. Growth kinetics of MAO coatings during oxidation in a complex electrolyte
The results of studying coatings in an alkali-silicate electrolyte are shown in Fig. 8-12. The results refer to the main hardened layer (the process layer is removed).
The dependence of the coating thickness on the oxidation time for two compositions of complex electrolytes is shown in Fig. 8. Treatment was carried out in electrolytes of the compositions KOH (1 g/L)+Na 2 SiO 3 (3 g/L) (dependence 1) and KOH (1 g/L)+Na 2 SiO 3 (6 g/L) (dependence 2) at a current density j=20 A/dm 2 . As can be seen from the data obtained, the kinetics of the formation of the coating thickness depends on the composition. In this case, the growth rate varies from V 1 g/L-KOH+3g/L-Na2SiO3 =0.875 µm/min to V 1 g/L-KOH+6g/L-Na2SiO3 =1.25 µm/min. Thus, the growth rate is within the optimal range for the formation of crystalline γ-Al 2 O 3 and α-Al 2 O 3 phases (Fig. 1, 5).
The linearity of the obtained dependence indicates that the thickness of the coating is proportional to the deposition time, and, accordingly, to the amount of electricity passed. In this case, as it was found experimentally, with a higher filling of the complex electrolyte with an alkaline or silicate component, the MAO treatment process turns into an arc Due to the higher growth kinetics, electrolysis in an electrolyte with the composition KOH (1 g/L)+Na 2 SiO 3 (6 g/L) was used as a base for further studies.

3. Phase composition and properties of MAO coatings during oxidation in a complex electrolyte
X-ray diffraction phase-structural analysis showed that the coatings obtained by microarc oxidation in an electrolyte with the composition KOH (1 g/L)+Na 2 SiO 3 (6 g/L) have a crystalline structure (Fig. 9). The main phases of the coating are the γ-Al 2 O 3 and α-Al 2 O 3 phases. The presence of a spectrum of peaks with a standard intensity from the planes of the crystalline phases indicates the absence of their preferred orientation (texture). The predominant phase at the beginning of the MAO process (at a small coating thickness) is γ-Al 2 O 3 . With an increase in the time of the MAO process and an increase in the coating thickness, a more complete polymorphic transformation γ-Al 2 O 3 →α-Al 2 O 3 occurs (Fig. 10).
Thus, as follows from the results shown in Fig. 10, in order to increase the content of the α-Al 2 O 3 phase in the MAO coating to 50 %, it is necessary to form a coating with a thickness of more than 100 µm. At a thickness of about 240 µm, the relative content of the α-Al 2 O 3 phase reaches 84 vol. %.
A change in the content of the α-Al 2 O 3 phase leads to a change in the hardness of the coatings (Fig. 11). In this case, a proportional increase in the hardness of the coating with an increase in the content of the α-Al 2 O 3 phase is observed.
Oxidation of the D16 alloy at different current densities (12-23 A/dm 2 ) showed that the thickness of the coating is determined by the amount of electricity passed, defined in A-hour/dm 2 (Fig. 12).
As seen from Fig. 12, the dependence of the coating thickness on the amount of transmitted electricity has two characteristic areas. The first section is in the range of 10-50 A-h/dm 2 , and the second -in the range of 50-120 A-h/dm 2 .  An analysis of the results obtained indicates that the choice of the type of electrolyte and the conditions for the process of microarc oxidation can significantly change the phase-structural state and surface properties of the D16 aluminum alloy. The use of an alkaline electrolyte (KOH) allows a significant increase in the power of microarc discharges, which contributes to the formation of the hardest α−Al 2 O 3 phase (Fig. 3, 4, a). This is a consequence of the completeness of the γ−Al 2 O 3 →α−Al 2 O 3 polymorphic transformation during the formation of coatings. In this case, the composition of the coating changes to the greatest extent with an increase in the duration of the process, reaching, with a duration of 180 min, compositions of 60 vol. % γ−Al 2 O 3 − 40 vol. % α−Al 2 O 3 (Fig. 5). The kinetics of the formation of such coatings increases with an increase in the KOH content in the electrolyte (Fig. 3). However, there is a limitation on the percentage of KOH content associated with the conditions for the formation of micro-arc discharges. It was found that an increase in the KOH content of more than 5 g/L does not ensure the implementation of the process in the mode of microarc discharges, which does not allow the formation of MAO coatings on the D16 alloy.
It should also be noted that the early results obtained for the AMg6 alloy, where Mg was the main alloying element (up to 5.8 %), showed that the γ−Al 2 O 3 →α−Al 2 O 3 transformation did not occur at all under similar conditions [48]. Thus, alloying of aluminum with copper is an important factor for the γ−Al 2 O 3 →α−Al 2 O 3 transformation. Although, in comparison with the AMg6 alloy, the rate of formation of the coating on the D16 alloy decreases. One of the reasons determining the noted features, apparently, is the low oxidizing ability of copper. However, to determine the mechanisms of such an effect, additional studies of the MAO process in alloys with different elemental compositions are required.
When using liquid glass (Na 2 SiO 3 ) as an electrolyte filler, the growth kinetics of the MAO coating increases (Fig. 6). However, an increase in the growth rate of the coating is accompanied in the silicate electrolyte by a decrease in the formation voltage, which leads to the formation of phases with a low density (mullite (3Al 2 O 3 •2SiO 2 ) and an amorphous-like phase, Fig. 4, b, 7).
The use of a complex alkali-silicate electrolyte allows, at a relatively low content (1 g/L KOH+6 g/L Na 2 SiO 3 ), forming a two-phase coating (γ−Al 2 O 3 and α−Al 2 O 3 ) at a relatively high growth rate of 1.25 µm/min (Fig. 8−10). At the same time, an increase in the duration of the process also makes it possible to increase the relative content of the α−Al 2 O 3 phase in the coating (Fig. 10). The hardness of such coatings increases with an increase in the content of the α−Al 2 O 3 phase and reaches 1,620 kg/mm 2 at a content of about 80 vol. % α-Al 2 O 3 phase (Fig. 11).
The dependence of the coating thickness on the amount of passed electricity has two characteristic areas (Fig. 12), which indicates two mechanisms of coating formation. The first of these mechanisms is manifested in the 10−50 A-hour/dm 2 section. As can be seen from the data obtained, in this area the dependence has an average ratio of 4.2 µm/(A-hour/dm 2 ). Such a large ratio of the coating thickness to the transmitted electricity is determined by the main mechanism in MAO treatment − the formation of a coating by the mechanism of electrochemical oxidation. In the second characteristic section, 50-120 A-hour/dm 2 , the average ratio of the coating thickness to the amount of passed electricity decreases to 1.1 µm/(A-hour/dm 2 ). The most probable reason for this decrease is the transition to a different mechanism of coating formation − the formation of a coating with the participation of electrolysis components. It is known that the formation of oxide as a result of deposition from the electrolyte leads to loose and poorly bonded coatings [49,50].
Thus, for an aluminum-based alloy with a copper content of about 4 wt. %, the use of an alkaline (KOH) electrolyte allows the formation of a two-phase (γ−Al 2 O 3 and α−Al 2 O 3 ) state. In this case, as the duration of the process increases, the relative content of the α−Al 2 O 3 phase increases. The use of a complex electrolyte makes it possible to increase the growth rate of such a coating and to a greater extent to proceed the reactions of the polymorphic transformation γ−Al 2 O 3 →α−Al 2 O 3 .
Thus, the results obtained can be used to improve the functional properties of aluminum alloys of the D16 type (an aluminum alloy with a copper content of about 4 wt. %). As follows from a comparison with the results obtained on the microarc oxidation of the AMg6 alloy [48], the use of other elements for alloying can significantly change the formation kinetics of the MAO coating and its phase composition. Therefore, in order to establish universal regularities for different types of aluminum alloys, further studies are required, which imply the determination of regularities in the structural-phase transformations of MAO coatings on aluminum alloys with metals, for which the oxidation energy is higher than for copper (V, Nb, Ta, and Cr).

Conclusions
1. It was found that for alkaline (KOH solutions) and silicate (Na 2 SiO 3 solutions) electrolytes, with an increase in the content of components, the growth rate of MAO coatings increases. With an increase in the KOH content from 1 g/L to 5 g/L, the growth rate of the coating increases from 0.33 to 1.33 µm/min. With an increase in the content of liquid glass from 10 g/L Na 2 SiO 3 to 50 g/L Na 2 SiO 3 , the growth rate increases from 1.08 to 2.25 µm/min. It was revealed that the phase composition of MAO coatings formed on the D16 alloy in alkaline (KOH) electrolyte consists of γ−Al 2 O 3 and α−Al 2 O 3 phases. An increase in the KOH concentration leads to a shift in the γ−Al 2 O 3 →α−Al 2 O 3 polymorphic trans- Amp-hours / dm 2 formation towards the formation of the hardest α−Al 2 O 3 phase (corundum). The addition of liquid glass (Na 2 SiO 3 ) in the electrolyte composition significantly increases the growth rate of the coating; however, the size of the ordering regions decreases from crystalline to X-ray amorphous.
2. It was determined that in a complex alkaline-silicate (KOH+Na 2 SiO 3 solutions) electrolyte, a growth rate of about 1 µm/min is achieved at a lower relative content of components. It was found that with an alkaline component (KOH) of 1 g/L and an increase in the silicate (Na 2 SiO 3 ) component of 3 g/L to 6 g/L, the growth rate of the MAO coating increases from 0.875 µm/min to 1.25 µm/min.
3. It is shown that the use of a complex alkaline-silicate electrolyte leads to a two-phase state of the coating with a large (compared to alkaline electrolyte) shift of the γ−Al 2 O 3 →α−Al 2 O 3 transformation towards the formation of the α−Al 2 O 3 phase. It was found that the value of the hardness of such coatings correlates with the content of the α−Al 2 O 3 phase in the MAO coating, reaching the highest value of 1620 kg/mm 2 at the highest content (about 80 vol. %) of the α−Al 2 O 3 phase. For MAO coatings obtained in a complex alkali-silicate electrolyte, two types of dependences of the coating thickness on the amount of electricity passed were revealed. For the amount of electricity passed 10-50 A-h/dm 2 , the thickness dependence is determined as 4.2 µm/(A-h/dm 2 ), which suggests the basic mechanism of electrochemical oxidation during the formation of a coating. For the amount of passed electricity 50-120 A-h/dm 2 , the thickness dependence is determined by a much lower value of 1.1 µm/(A-h/dm 2 ), which suggests a transition to a different mechanism of coating formation -the formation of a coating with the participation of electrolysis components.