Surface modifications of aluminium and aluminium oxide induced by a treatment with a He-plasma jet and plasma electrolytic oxidation

A SEM image of a polished untreated aluminium substrate is presented in figure 3. Figure 4 shows SEM images and EDS spectra of an analogous prepared aluminium substrate after a 5 min treatment with the He-plasma jet. Current–voltage characteristics of the treatment are very similar to those presented in [14] and are not presented here. During the treatment the distance between the nozzle of the plasma jet and the substrate surface amounts to 2 cm. No erosion traces are observed in the treated area with a radius of approximately 400 μm around the He-plasma jet axis. Near the border of this area, a thin oxide layer is deposited. The zoomed SEM image in figure 4 shows the structure of the surface and an EDS spectrum presents the material composition in this border area. The measured relative material composition in this area amounts to O: Al = 0.3.

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As variation, the effect of an additional He gas flow swirl on the plasma surface interaction is studied (figure 1(b)). A corresponding SEM image and an EDS spectrum measured on the aluminium substrate treated for 5 min with the He-plasma jet combined with an additional He gas flow swirl are presented in figure 5. Again, the treated area is approximately circular with a radius of 400 µm. Despite the absent of erosion traces in the middle of this treated area, at the edge of this area erosion traces and holes with the formation of aluminium oxide are observed. The measured relative material composition in this edge area amounts to O: Al = 1.4, which corresponds to a material composition close to aluminium oxide ceramic. The produced oxide appears as a layer with a very inhomogeneous structure and material composition (see zoomed SEM image and EDS spectra in figure 5).

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Based on results presented in [17] concerning the importance of a 'hot-spot' formation for plasma surface interactions and the enhancement of Ti layer erosion, a scratch on the aluminium surface is used in this work, which is artificially produced with a diamond blade. After scratching, the aluminium substrate is treated in the effluent of the He-plasma jet. During this treatment, the jet is moved along the scratch with a velocity of about 1 mms⁻¹. In several places erosion traces are located (see figure 6) near the scratch. An exemplary erosion area is presented in the zoomed SEM image in figure 6. Some structures with a material composition of O: Al = 1.3 can be detected, which can give a hint on oxide species. Also aluminium areas are observed in EDS spectra, illustrated in figure 6, as well. The comparably small peak at 2.12 keV in the EDS spectra is caused by a thin (approximately 13 nm) gold layer, which is deposited to exclude overcharging of the substrate surface during electron microscopy.

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Based on results presented in [22, 23], where microdischarges penetrate holes and thin slits in a dielectric and cause hydrocarbon erosion and crystals deposition, this effect is studied as a third option to enhance the erosion on an aluminium substrate. In those studies, the occurrence of plasmoids and their interplay with the substrate surfaces are mentioned to cause the erosion of hydrocarbon films with a high efficiency. To verify this assumption, a slit between two glass plates with polished edges is created (see figure 1(c)). These plates are directly placed on the aluminium substrate. The distance between the plate edges is measured with the electron microscope and amounts to approximately 20 μm. It is assumed, that the gap between the aluminium substrate and glass plates is in the same range. The He-plasma jet is used for a treatment of the top surface of the plates and is moved along the slit with a velocity about 1 mms⁻¹. After that, the dielectric glass plates are removed and the aluminium substrate is covered with a thin gold layer (about 13 nm) to exclude overcharging of the substrate surface during electron microscopy. The SEM image in figure 7 shows an exemplary segment of the aluminium substrate underneath the treatment area. The position of the slit edges is presented with dashed lines. The zoomed SEM image and the respective EDS spectra show the structure and the material composition of the treated aluminium surface in the slit area. The aluminium surface is modified not only in the slit region, but also in the area between the glass plates and aluminium substrate. In the presented SEM image (figure 7) areas with erosion traces are observed at a distance up to 85 μm from the slit centre. Consequently, microdischarges penetrate not only through the thin slit between the glass plates, but also spread in the slit between the glass plates and the aluminium substrate. The zoomed SEM image and EDS spectra in figure 7 present the surface structure and material composition (O: Al = 1.4) of a deposited aluminium oxide layer. Based on the velocity of the He-plasma jet movement along the dielectric slit and the width of the plasma spot on the dielectric surface a deposition rate can be roughly estimated. It is supposed to reach a high value of up to 10 μms⁻¹. After treating the glass plate with the plasma jet at a sufficiently large distance from the slit (10 mm), no erosion traces are observed on the aluminium substrate underneath the glass. Therefore, partial discharges in the gap between the dielectric glass and metal as a possible reason for the observed erosion and deposition of the oxide layer can be excluded from consideration [23].

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To compare the erosion mechanism of microdischarges at atmospheric pressure and during a PEO process, the interaction of the He-plasma jet with an aluminium oxide layer produced by anodising is studied. A SEM image of an exemplary aluminium substrate surface after 3 min anodising at a voltage of 250 V and a maximum current of 1 A is presented in figure 8. In comparison to the aluminium substrate shown in figure 3, the amorphous aluminium oxide film, grown on the aluminium substrate surface, gets visible (see figure 8). The measured ratio of the oxygen and aluminium density determined from EDS spectra amounts to O: Al = 0.9 and hence, differs from an expected value of 1.5 for aluminium oxide. A possible reason for this difference is the low thickness of the deposited oxide layer and the penetration depth of high energetic electrons of the electron microscope during EDS. The EDS detector of the used electron microscope collects information of the material composition from a depth of more than 1 μm. In the presented study, EDS delivers only qualitative information concerning material composition of substrate surface, since the resolution of the measurements is in the same range like the dimensions of the oxide layer of about 1 μm thickness and erosion structures at about 1 μm scale. Therefore, the measured EDS spectra and relative aluminium and oxygen intensities instead of numerical data concerning the material composition are presented in this study.

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The amorphous oxide film shown in figure 8 is strongly modified by a treatment with the He-plasma jet (see figure 9). Erosion traces appear as groups with different expansions on the treated surface (see figure 9(a)). Both, erosion craters and channels, can be observed on the treated surface. A form of craters produced with this treatment appears as eruption crater (see figure 9(c)) with a diameter of approximately 2 μm. The measured relative material composition at the borders of these erosion craters and channels amounts to about O: Al = 1.5. A characterisation of the material composition using the EDS spectrum in the hole shown in figure 9(c) is only possible, since the detection angle of the used SEM/EDS is small enough. Hence, the diameter of the hole combined with its comparable low depth is sufficient for a reliable EDS signal intensity.

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To better visualize the plasma interaction with the treated surface an additional gold layer is deposited before a plasma treatment based on results presented in [14, 16]. Similar to [16], a gold layer with a thickness of 100 nm on the surface of a pretreated aluminium substrate stops the erosion process completely. A relative thin gold layer (50 nm) influences erosion processes less, but also gives the possibility to observe the activity of microdischarges on the substrate surface with a high contrast [14]. A pre-anodised aluminium substrate (250 V, 0.125 Acm⁻², 3 min) covered with a 50 nm gold layer was treated with the He-plasma jet. The surface of the treated sample is studied with the electron microscope (see figure 10). In areas with a high number density of erosion traces the SEM images of the treated substrate surfaces with and without a thin gold layer are very similar, as can be seen in a comparison to figure 9. Because of the partial overlapping of different erosion traces, the interpretation of these images is very complicated. At the border of these areas, some separated erosion traces can be observed (see figure 10). These traces on the gold layer show a spatial distribution of temperature in a plasma spot of microdischarges and moving traces of microdischarges on the substrate surface during their lifetime and in an afterglow phase. Diameter of erosion traces at start and end points are different and can support an interpretation of the microdischarge activity on the treated surface. An interesting example of such microdischarge activity is shown in figure 10 (left), where the SEM image shows two microdischarge traces, with and without afterglow phase. The SEM image on right hand side of figure 10 shows large erosion areas mainly induced by plasmoids, which are formed in the afterglow of two microdischarges, which positions are marked with dashed circles.

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As before, to check the influence of a dielectric slit on the efficiency of erosion processes the experimental set-up presented in figure 1(c) is used. It is the same arrangement used for the previously shown enhancement of the erosion of uncoated aluminium (see figure 7). Now, the aluminium substrate was anodised at 250 V and a maximum current of 1 A (current density of 0.125 Acm⁻²) for 3 min and is treated with a He-plasma jet through the dielectric slit between two polished glass plates as presented in figure 1(c). During this experiment, the plasma jet is moved along the dielectric slit with a velocity of about 1 mms⁻¹. Similar to the treatment of uncoated aluminium, erosion traces and holes are distributed not only in the area of the slit, which width amounts to about 20 μm, but also under the glass plate up to 85 μm from the central axis of the slit (see figure 11). The measured relative material composition at the borders of erosion craters and channels amounts to about O: Al = 1.5. At the same time, mainly aluminium is found in the centre of broad eroded channels (see EDS spectrum on the left side of figure 11) and a low oxygen content is determined with EDS spectra measured inside of small eroded holes (O: Al ∼ 1.1). As before, no erosion traces can be observed on the substrate under the glass plate after a plasma treatment of the glass surface at a distance of approximately 10 mm from the slit.

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As comparison, an anodised aluminium substrate (250 V, 0.125 Acm⁻², 3 min) is treated with a short PEO process (750 V, 0.125 Acm⁻², duration 1 min). The high-speed camera image in figure 12 shows the PEO microdischarges, which are mainly distributed near the substrate edges of the treated substrate during this short process. Corresponding SEM images and EDS spectra reveal the surface structure and material composition of the substrate top layer as shown in figure 13. The structure of this surface shows similarities to the structure of a substrate surface treated with the He-plasma jet presented in figures 10 and 11. Both, erosion craters and long erosion traces with comparable dimensions, can be observed in these images. The long microdischarge erosion traces are characterised by a thin molten and solidified layer, which can be observed in both SEM images in figure 13. EDS spectra presented in figure 13 show, that the amount of oxygen increases in these long erosion traces compared to nearby not molten areas with a ratio of oxygen to aluminium of O: Al = 1.1–1.3. The ratio of oxygen to aluminium at microdischarge crater cones and inside of craters amounts to 1.5 and 0.8, respectively.

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Analogous to the previous He-plasma jet treatment, a thin gold layer on an anodised surface is used to observe the microdischarge activity during a PEO process. Therefore, the anodised aluminium substrate (250 V, 0.125 Acm⁻², 3 min) is covered with a thin gold layer (5 mm × 5 mm × 50 nm) in the middle of a substrate by using a silicone mask and afterwards treated with a short PEO process (750 V, 0.125 Acm⁻², 40 μs). The gold layer causes a decrease of the ignition voltage of microdischarges below 200 V. Because of the short duration time of this treatment and the small dimension of the gold layer, it is possible to observe the ignition of all single microdischarges. This enables a correlation of single microdischarges and erosion traces left by these microdischarges on the substrate surface using a high-speed camera and electron microscopy (see figure 14). Microdischarges of varying intensity and varying form and size are observed with a high-speed camera. Corresponding SEM images reveal both, deep microdischarge craters and long shallow erosion traces, shown in the second row of figure 14.

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To study a deep and shallow erosion caused by PEO microdischarges on a thick oxide film, an aluminium substrate was prepared with a long PEO process (750 V, 0.125 Acm⁻²) of 30 min duration and covered with a thin gold layer (50 nm), as before. Afterwards, this substrate was treated with a short PEO process (750 V, 0.125 Acm⁻², 40 µs). Similar microdischarges as on a thin oxide film can be observed during this short treatment by using the high-speed camera. But in contrary, no deep erosion traces are established on the gold coated substrate surface. Shallow erosion traces in the gold layer can be found mainly near the cracks of the former oxide layer (see figure 15). Some of these microdischarges seem to induce long shallow erosion traces with a broadness of approximately 2 μm. No remarkable damages of the underlying oxide layer can be observed in the traces of these microdischarges near cracks and in the long shallow erosion traces.

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A similarly prepared aluminium substrate (750 V, 0.125 Acm⁻², 30 min) with an additional gold layer is treated with the He-plasma jet. Corresponding SEM images of the treated surface show both, deep craters and shallow erosion channels (see figure 16). The deep erosion craters can be found along the cracks of the prepared oxide layer. The dimension of the observed erosion craters and shallow erosion traces are similar to the dimensions of erosion traces induced by microdischarges of the short PEO process presented in figure 15.

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Based on the knowledge of the interaction of the DBD-like plasma jet with different substrate materials like aluminium oxide [14], aluminium [16], titanium [17] and silicon [24, 25], a plasma-induced oxidation on the surface of an aluminium substrate is considered in this work. This will lead to further information about how microdischarges can interact with material surfaces and may contribute to an understanding of plasma-induced oxidation processes of surfaces for various applications. In general, a direct oxidation of an aluminium surface or oxide layer creation with the considered He-plasma jet is inefficient. This result was expected, since aluminium oxidation needs a high temperature or long treatment duration [26]. Because of the nanosecond microdischarge duration and, therefore, low surface temperatures of the substrate area treated with the He-plasma jet, a low erosion rate of aluminium is observed. Due to a reduced oxygen content in the gas flow (after diffusion of surrounding air), a very low oxide growth rate can be determined on a flat aluminium surface (see figure 4). Based on the results of [17, 22], the erosion rate in the effluent of the DBD-like plasma jet can be enhanced by a gas flow swirl on the substrate surface, the formation of artificial 'hot spots' on the treated surface and an application of a thin dielectric slit on the treated surface. In the frame of this work it could be shown, that all these methods cannot only enhance erosion processes, but also the oxidation of the surface or deposition of an oxide layer by a treatment with the He-plasma jet (see figures 5–7). The oxidation/deposition rate as well as the oxidised/deposited area are small in the case of an additional swirling gas flow and the formation of a 'hot spot' by scratching the substrate surface. These results are comparable to results presented in a previous study [17], where a formation of titanium oxide by a plasma treatment with the presented jet operated with argon flow was studied. However, a considerably higher deposition rate of aluminium oxide up to 10 μm·s⁻¹ is detected after a plasma treatment of the He-plasma jet through an additional dielectric slit (see figure 7). Artificial 'hot spots' produced by scratching the substrate surface and the application of a dielectric slit can cause the formation of several ionisation and shock waves, which propagate with different velocities and cause a formation of micro-vorticies [27, 28]. If a dielectric slit, like in the presented experiment, is in the propagation path of an ionisation wave of a microdischarge, it can cause a wave separation leading to the formation of two ionisation waves with different velocities, one with a high velocity over the dielectric surface inside of the slit and one with a low velocity in the gas volume. As was mentioned before, interactions of ionisation waves can cause the formation of micro-vortices [27] and provide an initial situation for gas vortex-plasma interactions [29]. At a certain vortex velocity this effect causes the formation of a plasma plume or plasma lump [29, 30] and can cause toroidal heating and deep erosion of the treated surface [18]. An additional consequence of vortex-plasma interactions is the formation of plasmoids [19, 29], which can cause short cutting of plasma channels (see e.g. [29]) or leave shallow erosion traces on the treated surface (see e.g. [17]). These effects resulting from vortex-plasma interactions are very likely the reason for PEO-like surface structures formed during the He-plasma jet treatment through a dielectric slit. During PEO micro-vortices could be formed from gas evolving in the oxide layer and streaming through pores.

The inhomogeneity of the deposited aluminium oxide film is a disadvantage of the He-plasma jet treatment (see figure 7). A possible reason for this effect is a transport of produced oxide with a microdischarge or its afterglow (plasmoids), which causes the formation of aluminium oxide clots. A similar effect was established in previous studies considering plasma jet-surface interactions [16, 22, 25]. The reason of this effect is not clear now and must be studied additionally. The next disadvantage of oxide layer deposition with an atmospheric pressure plasma jets is the only local surface treatment. An easy broadening of the plasma jet effluent cannot solve this problem, because the formation of microvortices and a contraction of the plasma spot down to a micrometer scale are required conditions for an effective oxide layer deposition, as was shown before. A possible solution for this problem is a parallel application of plasma jets [13].

A possible interesting application of a plasma jet for the deposition of oxide films is the formation of thick porous film for biomedical applications [31]. As was shown in figure 16, a thick oxide film, for example deposited with a PEO process, can be locally modified by a short treatment with a rare gas plasma jet. At that, erosion holes with a diameter of 1 μm–2 μm are produced. Number density of the erosion holes and their positions on the treated object can be easily optimised by varying the treatment duration and plasma jet position.

Microdischarges ignited on a substrate surface in the effluent of the He-plasma jet and during a PEO process are operated in different gas mixtures. This difference is obvious, since no helium is involved in the PEO process. Measured emission spectra of the used plasma sources can be found in a previous work [14]. Moreover, based on measurements on single microdischarges in different electrolytes and on different substrate materials [9, 10], it can be concluded, that the duration of PEO microdischarges amounts to several tens of microseconds. This is about three orders of magnitude longer than microdischarges in the effluent of rare gas plasma jets, which duration amounts to about 100 ns. On the other hand, many other properties of PEO and He-plasma jet microdischarges are very similar and suggest the assumption of a principal comparability of these microdischarges.

The inhomogeneity of both microdischarges and the formation of a plasma core was established in different experiments. The visible diameter of PEO microdischarge plasmas observed with the CCD camera amounts to 100 μm–200 μm (see figure 12). This value is similar to microdischarge diameter during short PEO processes measured in other experiments (see e.g. [7]). The diameter of a plasma spot on the surface of a substrate treated with Ar- and He-plasma jets amounts to 300 μm–600 μm [14, 16, 24]. In contrary, the diameter of erosion traces measured with the electron microscope on the substrates treated with both microdischarges amounts to 1 μm–2 μm, namely more than two orders of magnitude smaller. A determination of the plasma temperature and the electron density in PEO microdischarges testifies the formation of a plasma core with a high gas temperature and high electron density [1]. Based on the similarities of microdischarge currents measured in our experiment and in other studies [9, 10, 16] and similarities of the dimension of erosion traces left by PEO microdischarges and the He-plasma jet, it can be concluded, that microdischarge current densities, determined as the ratio of current values through the averaged cross section of erosion holes, are also similar. In case of PEO, the maximum current of a single microdischarge is in the range of 100 mA [9]. This is in the same range like current signals measured during the operation of the plasma jet [16]. Therefore, current densities in the range of 10⁷ Acm⁻² can be determined assuming a diameter of erosion traces of about 1 µm.

A formation of plasmoids in the afterglow phase of microdischarges is a characteristic property of an etching process during the interaction of a rare gas plasma jet with a substrate surface. The shallow etching traces left by these plasma objects were observed in different studies (see e.g. [16, 17, 24, 25]. Comparable shallow etching traces with similar length and cross section are observed also near deep erosion traces of PEO microdischarges after the addition of a thin gold layer (see figures 14 and 15). As was mentioned before, a gold layer with a low thickness of approximately 50 nm on an aluminium oxide substrate surface does not inhibit erosion processes, but enables an observation of plasma activity (see figure 14) and spatial distribution of the treated surface temperature [14]. In this context, two properties of gold are fundamental for the performed measurements, namely, the secondary electron emission of gold is considerably higher than of aluminium oxide and the melting point of gold (1336 K) is between the melting point of pure aluminium (933 K) and aluminium oxide (2345 K). The secondary electron emission gives the possibility to detect erosion traces of microdischarges on the treated surface with a high contrast using electron microscopy. The different melting points of deposited materials give hints for an estimation of a temperature distribution on the surface of substrates during microdischarge-surface-interactions. A characteristic example of an erosion trace is presented in figure 10 (left). The EDS spectrum of the deep erosion trace (diameter 1 μm–2 μm) shows that almost pure aluminium is placed on the bottom of erosion crater. At the same time, the SEM image shows that the surface of this aluminium is very rough. This leads to the conclusion, that the aluminium inside of such eroded holes is not melted, because melted and solidified aluminium exhibits a surface of solidified fluid, which can be observed in some other erosion traces left by microdischarges of the PEO process and the He-plasma jet. However, based on measured EDS spectra it can be concluded, that the crater cone is formed by melted and solidified aluminium oxide. The thin gold layer is melted in a circular area around erosion craters to diameter of 5 μm–10 μm. Based on these spatial distribution of eroded traces, a toroidal heating of the surface treated with both microdischarges of PEO and He-plasma jet is assumed. A temperature lower than 900 K is assumed in the circular area near the microdischarge axis with a diameter of 1 μm–2 μm, which is surrounded with a toroidal area heated higher than 2300 K (broadness of about 1 μm) and an attached toroidal area heated between 1300–2300 K (broadness about 2 μm). Comparable toroidal heating using microdischarges ignited by an interaction of a filamentary plasma with gas flow vortices was observed during the treatment of a Ti-layer with an Ar- and Kr-plasma jet [17] and after an interaction of a gliding arc channel with a stainless steel electrode of a plasmatron [18].

As was mentioned before, both microdischarge sources produce plasmoids in an afterglow phase, which left long erosion traces with a broadness of about 2 μm. Such long erosion traces can be observed in figures 10 and 14–16. Based on SEM and EDS studies a process surface temperature between 1300 K and 2300 K is assumed at all traces of plasmoids, which are produced by these microdischarges. A similar effect was established in [24, 25], where plasmoids, which are produced by rare gas plasma jets on the surface of silicon, left amorphous silicon in eroded traces and therefore, do not melt the silicon substrate, which melting point amounts to 1687 K.

Comparing figures 9, 11 and 13 it can be concluded, that the material composition inside and near eroded traces left on the treated surface by a PEO process and the He-plasma jet are very similar. An additional production of a thin oxide layer near the microdischarge axis during the PEO process can be explained by an anodisation of the aluminium surface in contact with the electrolyte after a microdischarge at PEO conditions.

To summarise, in a former study [14] the similarities of erosion traces on plasma-treated aluminium and aluminium oxide substrates lead to the assumption of a similar material erosion mechanism induced by microdischarges during a PEO process and atmospheric pressure plasmas. This assumption is confirmed in the presented study, especially considering the comparison of erosion traces produced by PEO microdischarges and the He-plasma jet on aluminium oxide layers covered with a thin gold layer. These simultaneous studies of microdischarges at both plasma conditions enable on the one hand a better understanding and possibly optimisation of the PEO process. On the other hand, this method gives the possibility to observe microdischarge mechanisms like the evolution of a microdischarge core and plasmoid formation from different point of views, since PEO microdischarges can be observed in top view while the plasma jet can be studied mostly in side view.

The known microdischarge characteristics of the rare gas plasma jet, which can be helpful for an interpretation of the PEO process based on the above mentioned similarity of the erosion mechanism are the following: (i) an extraction of light atoms of the treated substrate material near the microdischarge axis (without melting) [16, 17], (ii) a toroidal heating of the treated material up to several thousand Kelvin [17, 18], (iii) a formation of plasmoids in an afterglow phase [16, 17, 23–25].

Based on results presented in [17], the oxygen content of glass and aluminium oxide treated with a rare gas plasma jet is reduced by a factor of about 3.5 and 5, respectively. At that, nitratine crystals with a low temperature boiling point (653 K) can be observed in the middle of erosion trace. The melted and solidified titanium and titanium oxide (melting points are 1940 K and 2110 K, respectively) are observed at the edges of erosion traces. Based on the assumption of an erosion mechanism similarity, an extraction of oxygen in the middle of erosion holes induced by microdischarges during the PEO process is proposed with a simultaneous melting of erosion holes' edges. This effect can explain the extreme high efficiency of the oxygen production during PEO processes [1] and the formation of ceramic bubbles, which can be often observed on the treated surfaces as can be exemplary seen in figures 13 (right) and 17.

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The development and propagation of microdischarges in cracks and pores and the erosion of aluminium oxide inside of cavities in the oxide layer is very important for the PEO process, especially during long time treatments. An established model of PEO microdischarges was introduced by Hussein et al [32] and extended by Cheng et al [33]. The model classifies microdischarges as type A, B, C, D and E microdischarges appearing at different positions on the coating surface and inside the coating. Destructive type B and type E discharges are supposed to pass the whole or at least outer coating and produce large coating defects like holes. At the same time, type A and C discharges are supposed to be less strong, which could be interpreted as less intense optical emission and lower microdischarge currents. Additionally, the introduced type D microdischarges are supposed to be in the inner coating layer and therefore, not optically observable. Based on results of [33, 34] it was assumed that during long-time deposition processes, microdischarges inside of cavities cause the erosion of the oxide and aluminium substrate and induce an upward growth of the coating. Figures 15 and 16 show SEM images of an aluminium oxide layer pretreated with a PEO process with a duration of 30 min covered with a 50 nm gold layer and treated again with short PEO process (figure 15) and with the He-plasma jet (figure 16). No deep erosion traces are observed on the surface of these thick aluminium oxide layer despites photoemission of microdischarges, which can be detected with the high-speed camera. Shallow erosion traces are observed mostly near the cracks in the oxide layer. Some of these microdischarges seem to produce plasmoids, which leave the shallow erosion traces of different length. Considering the results from the He-plasma jet on the slit created by two glass plates, it is assumed, that microdischarges on the top of cracks in the dielectric aluminium oxide coating cause discharge propagation into these cracks and a treatment of the inner aluminium oxide layer or aluminium substrate without a formation of deep erosion traces with eruption craters on the outer surface. This is consistent with erosion defects of the surface on the inner layer of PEO coatings shown in [33].