# Characterisation of PMMA/ATH Layers Realised by Means of Atmospheric Pressure Plasma Powder Deposition

Authors: Lena M. Wallenhorst; Sebastian Dahle; Matej Vovk; Lisa Wurlitzer; Leander Loewenthal; Nils Mainusch; Christoph Gerhard; Wolfgang Viöl
Journal: Advances in Condensed Matter Physics
 (2015)

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## Abstract

We report on the characteristics of aluminium trihydrate filled poly(methyl methacrylate) composite (PMMA/ATH) coatings realised by plasma deposition at atmospheric pressure. For this purpose, PMMA/ATH powder was fed to a plasma jet where the process and carrier gas was compressed air. The deposited coatings were investigated by X-ray photoelectron spectroscopy and water contact angle measurements. Further, the raw material was characterised before deposition. It was found that, with respect to the raw material, aluminium was uncovered in the course of the plasma deposition process which can be explained by plasma-induced etching of the PMMA matrix. As a result, the wettability of plasma-deposited PMMA/ATH was significantly increased. Even though a uniform coating film could not be realised as ascertained by confocal laser scanning microscopy, the deposited coatings feature notably enhanced characteristics which could be advantageous for further processing.


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## Body

## 1. Introduction

The application of inorganic fillers as reinforcement within polymer composites is a well-known approach [1] that is still commonly applied [2]. One particular composite material that has been continuously improved in the past decades and is still having an increasing number of applications is poly(methyl methacrylate) (PMMA) reinforced with aluminium trihydrate (Al(OH)3, ATH). The PMMA/ATH composite is classified as solid material [3] and was developed and described by Duggins and coworkers [4, 5]. Several different compositions and fabrication processes are commonly in use, but in general PMMA/ATH composites consist of about 40% PMMA and 60% ATH. All composites of this kind feature high moisture resistance, good chemical resistance, and UV resistance. They are safe for food contact, easy to clean, and thermoformable [6, 7]. The ATH used as inorganic filler within the composite lowers the costs for the fabrication of this material and further drastically improves the mechanical properties such as elastic modulus [8], abrasion, and wear resistance [9] as well as the fatigue life [10]. The ATH also acts as a flame retardant and smoke suppressant [11–13].For many applications, ATH filler particles with average sizes of approximately 2–10μm are used, which typically occur as agglomerates of 40–50 μm [14]. Otherwise, bead milling can be used to ensure an average filler particle size below 1 μm, consequently improving the distribution of the filler particles within the matrix [15]. Furthermore, silane coupling agents [16] are usually applied to ensure an excellent dispersion [15] and enhance the mechanical properties [9, 10] as well as the thermal stability of the composite material [15].However, the final processing of PMMA/ATH composite materials may be complicated. For example, it has been found to be quite challenging to form a structural joint via bonding of PMMA/ATH material with wood and wood composites [17]. Another open issue is the recycling of PMMA/ATH composite materials. The shaping and polishing of PMMA/ATH work pieces produce an estimated amount of 1200 tons of PMMA/ATH waste dust per year only in Slovenia [18]. Even though the material itself exhibits outstanding mechanical and chemical properties, residual powder and chips can hardly be used in an industrial and economically viable way. Kaminsky and colleagues [19] have carried out the pyrolysis of a PMMA/ATH composite. Pyrolysis of PMMA is already an established way of obtaining methyl methacrylate monomer (MMA), because at 450°C as much as 97.2% of MMA can be obtained. Authors investigated if it is possible to obtain similarly high proportions of MMA from PMMA/ATH composites with high content of ATH and whether there is a catalytic effect of ATH in the process of pyrolysis. The results showed that the pyrolysis of the PMMA/ATH obtained only 58% of the MMA, which is a much smaller percentage compared to 97%, which was obtained from pure PMMA. By-products of the thermal decomposition of this composite were the hydrolysis products of MMA, such as methacrylic acid, methanol, and isobutyl acid. By lowering the temperature to 400°C, they have managed to increase the obtained MMA to 65% by weight. They found that such a low proportion of acquired MMA is a consequence of the water released from the pyrolysis of ATH and chemical stabilizers in the composite. The high proportion of aluminium components practically has no catalytic effect on hydrolysis, because they got the same results by using the water vapour as fluidising medium instead of nitrogen [19]. However, some innovative approaches recently try to make use of the waste powder, for example, as filler for bitumen [18].In a recent approach, the use of a dielectric barrier discharge (DBD) plasma for the modification of PMMA/ATH work pieces has been evaluated, that is, trying to functionalise the PMMA/ATH surface and to improve the bonding of glues and other polymers to the modified PMMA/ATH surface. In the literature, several effects of cold plasma discharges on PMMA are reported, namely,(a)
an oxidation of the polymer [20],(b)
a homogeneous etching of the polymer [21],(c)
a generation of micro- or nanopatterns on the polymer’s surface [22].All of these effects could be promising for an enhancement of the bonding strength upon gluing as well as for the use of the processed powder as additive to polymer resins. The oxidation of the polymer (a) should happen by the attachment of polar groups, which could then probably act as chemical interlinks between binder and substrate or between composite powder and polymer matrix. The homogeneous etching (b) could lead to exposed ATH particles, allowing an improved attachment of an adhesive or a polymer matrix to the ATH’s hydroxyl groups. Thus, these partially exposed filler particles would presumably act as mechanical interlocking and most likely lead to an improved bonding strength via form closure. The inhomogeneous etching (c), that is, the formation of rough micro- and nanostructures, should at least lead to a mechanical interlocking between adhesive and substrate or between composite powder and polymer matrix. However, these expectations were not fulfilled by a DBD pretreatment of PMMA/ATH work pieces. Even though some carboxy groups at the outermost surface layer of the PMMA as well as an increased surface roughness did remarkably reduce the water contact angles, no significant impact on bonding strengths with a water-based adhesive was observed. Due to formation of debris on the surface, representing the weakest link, an increase in bonding strength was prevented. The stability of the bonds against humidity was significantly improved, but still this does not yield any new possibilities for the use of the PMMA/ATH waste powder.Following these previous results, the results of a plasma treatment of the waste powder using a gliding arc discharge are presented in this contribution. The gas temperatures of gliding arc discharges are usually in the order of magnitude of 1000 K and above [23], while the increase of sample temperatures during DBD plasma treatments usually would not exceed 10 K [24]. Correspondingly, the etching rates for the polymer are expected to be significantly higher in comparison to the previous approach. As a result, the formation of significant amounts of debris might be inhibited. Furthermore, the presented approach employs remote plasma to directly process the waste powder within a gas stream and concurrently deposit the powder onto a surface.Remote plasma devices, that is, plasma jets, already have been employed to deposit films onto PMMA substrates via plasma-enhanced chemical vapour deposition [25]. Furthermore, the use of remote plasma devices for the functionalization of aerosol particles has been demonstrated before, for example, for polyethylene particles [26]. The approach to use remote plasma for both a functionalization of aerosol particles and the concurrent deposition of these particles as a functional coating, however, has not yet been reported in literature.


## 2. Characterisation of the Used PMMA/ATH Powder

In this work, aluminium trihydrate-reinforced poly(methyl methacrylate) powder from Kolpa, d.d., Slovenia, was used for the realisation of PMMA/ATH layers by atmospheric pressure plasma powder deposition. The mechanical properties of original PMMA/ATH composite boards were already investigated by other groups, yielding a densityρ of 1740 kg/m3 and a filler particle fraction of 50 wt.% ATH [18], as well as a modulus of elasticity E of approximately 9700 N/mm2 and a bending strength S of approximately 70 N/mm2 [17]. In addition, the constant wetting rate angle (CWRA), the surface energy, the particle size distribution, and the specific surface areas as well as the glass transition temperature were determined in the present work prior to plasma deposition.


### 2.1. Determination of the Constant Wetting Rate Angle (CWRA) and Surface Energy

For the determination of the constant wetting rate angles of distilled water and diiodomethane drops on the used PMMA/ATH powder, a Krüss Drop Shape Analyser, DSA100, was used. Prior to applying the drops on the samples, the powders were pressed using a hand press Graseby from Specac. In this vein, circular plates with a diameter of 13 mm and a mass of 275 ± 5 mg were produced where the pressing time was 10 s and the pressing pressure was 739.46 N/mm2. The volume of the applied drops was 1-2 μL. The process of applying the drops on the substrates was recorded and each drop was subsequently analysed by a circle fitting method from which the contact angle was calculated. Subsequently, the surface energies were determined using the measuring system’s Drop Shape Analyser and an implemented evaluation algorithm according to Owens, Wendt, Rabel, and Kaelble (OWRK) [27], which is based on Young’s equation, given by(1)γSG=γSL+γLGcos⁡θ.Here, γSG is the interfacial energy between solid and gas, γLG between liquid and gas, and γSL between solid and liquid. According to the OWRK method, the total energy γtot is the sum of polar (γP) and disperse (γD) fraction. Distilled water (γtot=72.8 mNm−1, γP=51 mNm−1, and γD=21.8 mNm−1 at T=20°C) and diiodomethane (γtot=50.8 mNm−1, γP=0 mNm−1, and γD=50.8 mNm−1 at T=20°C) were used to analyse the constant wetting rate angle on the pressed PMMA/ATH powder pellets and to determine its surface energy. The angles were determined after a transition time of 3 s after application of the drops since it was visually established that this time interval coincides with the transition from the spreading stage to a constant penetration regime, basically following [28]. All measurements were performed at an environmental humidity of 35 ± 2% and a temperature of 22 ± 1°C. By this procedure, a constant wetting rate angle of 66.94° ± 0.95° for distilled water was measured, where the overall surface energy was 49.23 mNm−1, given by the sum of the disperse fraction of 40.65 mNm−1 and the polar fraction of 8.57 mNm−1.


### 2.2. Determination of the Particle Size Distribution and Specific Surface Areas

The particle size distribution of the powder was determined by laser light scattering with the aid of a particle analyser Mastersizer S from Malvern Instruments. A 300RF lens with a QS small volume sample dispersion unit for measuring liquid dispersion was used. The obscuration was adjusted to 12–15%. Powder samples were dispersed in distilled water using an ultrasonic probe. The dispersion was sonicated for 3 minutes prior to the measurement. Particle size distributions typically includeD(0.1), D(0.5), and D(0.9), which represent the percentages of particles (i.e., 10%, 50%, and 90%, resp.) below the given size in microns. By applying the above-described procedure, the particle size distribution was determined to D(0.1)=7.23 μm, D(0.5)=75.66 μm, D(0.9)=167.82 μm, and D(max)=301.68 μm.The specific surface areas of PMMA/ATH powders were determined via Brunauer-Emmet-Teller (BET) nitrogen adsorption at 77 K from the adsorption data in the relative pressure interval fromp/p0=0.05 to 0.3. For this measurement, a nitrogen adsorption analyser Tristar 3000 from Micromeritics Instruments was used. Prior to the measurements, between 150 and 250 mg of the sample were accurately weighed into sample tubes and degassed overnight at 50°C in a vacuum dryer VacPrep 061 from Micromeritics Corporation. In the course of this drying process, the temperature was set to 50°C in order to avoid possible thermochemical reactions of the samples. Two replicate measurements were carried out to evaluate the reproducibility. As a result, a BET specific surface of 2.1452 ± 0.0250 m2/g was determined.


### 2.3. Determination of the Glass Transition Temperature

The glass transition temperature of the used polymer composite powder was determined by differential scanning calorimetry (DSC). A commercial setup DSC 820 from Mettler-Toledo International Incorporation was used to measure in steps of 10 K within a temperature range from −10°C to 250°C. During the measurement, technical nitrogen was used as cover gas. To minimise the influence of impurities and residuals, two heating curves and a cooling curve were recorded sequentially, while only the second heating curve was used for the analysis.The measured DSC curves are shown in Figure1, representing the curves of both heating cycles as well as the cooling process in between. A detailed view of the relevant second heating curve is given in Figure 1(b), depicting a glass transition temperature Tg of about 120°C.Figure 1
DSC sequential heating and cooling curves for an untreated PMMA/ATH powder (a) as well as a detailed view of the second heating curve (b).
(a)
(b)The elevated value for the PMMA/ATH in comparison to the literature value of pure PMMA of 105°C [29] is most probably due to the interface between the PMMA matrix and the ATH filler particles [30]. Furthermore, the glass transition temperature is dependent on the mobility of the polymer chains within the matrix. Generally, a large number or length of linear polymers’ side chains leads to decreased glass transition temperatures, while stiff polymers exhibit low mobility and thus high glass transition temperatures. Accordingly, hard filler particles within the polymer matrix lead to a reduced mobility of the polymer chains and thus the glass transition temperature usually increases with an increasing content of filler material [31].


### 2.4. Summary of PMMA/ATH Powder Material Properties

To summarise, the material properties of PMMA/ATH powder which was used for atmospheric pressure plasma deposition as presented hereafter are listed in Table1.Table 1
Material properties of the PMMA/ATH powder used for atmospheric pressure plasma deposition.
Parameter
Value
Ash residue in wt.%
53.4
Constant wetting rate angle (CWRA) in degrees
66.9  ± 0.95
Total energyγtot in mNm−1
49.2
Disperse fractionγD of γtot in mNm−1
40.6
Polar fractionγP of γtot in mNm−1
8.5
D
(
0,1
) in μm
7.2
D
(
0,5
) in μm
75.6
D
(
0,9
) in μm
167.8
D
(
max
⁡
) in μm
301.6
Glass transition temperatureTg in °C
120


## 2.1. Determination of the Constant Wetting Rate Angle (CWRA) and Surface Energy

For the determination of the constant wetting rate angles of distilled water and diiodomethane drops on the used PMMA/ATH powder, a Krüss Drop Shape Analyser, DSA100, was used. Prior to applying the drops on the samples, the powders were pressed using a hand press Graseby from Specac. In this vein, circular plates with a diameter of 13 mm and a mass of 275 ± 5 mg were produced where the pressing time was 10 s and the pressing pressure was 739.46 N/mm2. The volume of the applied drops was 1-2 μL. The process of applying the drops on the substrates was recorded and each drop was subsequently analysed by a circle fitting method from which the contact angle was calculated. Subsequently, the surface energies were determined using the measuring system’s Drop Shape Analyser and an implemented evaluation algorithm according to Owens, Wendt, Rabel, and Kaelble (OWRK) [27], which is based on Young’s equation, given by(1)γSG=γSL+γLGcos⁡θ.Here, γSG is the interfacial energy between solid and gas, γLG between liquid and gas, and γSL between solid and liquid. According to the OWRK method, the total energy γtot is the sum of polar (γP) and disperse (γD) fraction. Distilled water (γtot=72.8 mNm−1, γP=51 mNm−1, and γD=21.8 mNm−1 at T=20°C) and diiodomethane (γtot=50.8 mNm−1, γP=0 mNm−1, and γD=50.8 mNm−1 at T=20°C) were used to analyse the constant wetting rate angle on the pressed PMMA/ATH powder pellets and to determine its surface energy. The angles were determined after a transition time of 3 s after application of the drops since it was visually established that this time interval coincides with the transition from the spreading stage to a constant penetration regime, basically following [28]. All measurements were performed at an environmental humidity of 35 ± 2% and a temperature of 22 ± 1°C. By this procedure, a constant wetting rate angle of 66.94° ± 0.95° for distilled water was measured, where the overall surface energy was 49.23 mNm−1, given by the sum of the disperse fraction of 40.65 mNm−1 and the polar fraction of 8.57 mNm−1.


## 2.2. Determination of the Particle Size Distribution and Specific Surface Areas

The particle size distribution of the powder was determined by laser light scattering with the aid of a particle analyser Mastersizer S from Malvern Instruments. A 300RF lens with a QS small volume sample dispersion unit for measuring liquid dispersion was used. The obscuration was adjusted to 12–15%. Powder samples were dispersed in distilled water using an ultrasonic probe. The dispersion was sonicated for 3 minutes prior to the measurement. Particle size distributions typically includeD(0.1), D(0.5), and D(0.9), which represent the percentages of particles (i.e., 10%, 50%, and 90%, resp.) below the given size in microns. By applying the above-described procedure, the particle size distribution was determined to D(0.1)=7.23 μm, D(0.5)=75.66 μm, D(0.9)=167.82 μm, and D(max)=301.68 μm.The specific surface areas of PMMA/ATH powders were determined via Brunauer-Emmet-Teller (BET) nitrogen adsorption at 77 K from the adsorption data in the relative pressure interval fromp/p0=0.05 to 0.3. For this measurement, a nitrogen adsorption analyser Tristar 3000 from Micromeritics Instruments was used. Prior to the measurements, between 150 and 250 mg of the sample were accurately weighed into sample tubes and degassed overnight at 50°C in a vacuum dryer VacPrep 061 from Micromeritics Corporation. In the course of this drying process, the temperature was set to 50°C in order to avoid possible thermochemical reactions of the samples. Two replicate measurements were carried out to evaluate the reproducibility. As a result, a BET specific surface of 2.1452 ± 0.0250 m2/g was determined.


## 2.3. Determination of the Glass Transition Temperature

The glass transition temperature of the used polymer composite powder was determined by differential scanning calorimetry (DSC). A commercial setup DSC 820 from Mettler-Toledo International Incorporation was used to measure in steps of 10 K within a temperature range from −10°C to 250°C. During the measurement, technical nitrogen was used as cover gas. To minimise the influence of impurities and residuals, two heating curves and a cooling curve were recorded sequentially, while only the second heating curve was used for the analysis.The measured DSC curves are shown in Figure1, representing the curves of both heating cycles as well as the cooling process in between. A detailed view of the relevant second heating curve is given in Figure 1(b), depicting a glass transition temperature Tg of about 120°C.Figure 1
DSC sequential heating and cooling curves for an untreated PMMA/ATH powder (a) as well as a detailed view of the second heating curve (b).
(a)
(b)The elevated value for the PMMA/ATH in comparison to the literature value of pure PMMA of 105°C [29] is most probably due to the interface between the PMMA matrix and the ATH filler particles [30]. Furthermore, the glass transition temperature is dependent on the mobility of the polymer chains within the matrix. Generally, a large number or length of linear polymers’ side chains leads to decreased glass transition temperatures, while stiff polymers exhibit low mobility and thus high glass transition temperatures. Accordingly, hard filler particles within the polymer matrix lead to a reduced mobility of the polymer chains and thus the glass transition temperature usually increases with an increasing content of filler material [31].


## 2.4. Summary of PMMA/ATH Powder Material Properties

To summarise, the material properties of PMMA/ATH powder which was used for atmospheric pressure plasma deposition as presented hereafter are listed in Table1.Table 1
Material properties of the PMMA/ATH powder used for atmospheric pressure plasma deposition.
Parameter
Value
Ash residue in wt.%
53.4
Constant wetting rate angle (CWRA) in degrees
66.9  ± 0.95
Total energyγtot in mNm−1
49.2
Disperse fractionγD of γtot in mNm−1
40.6
Polar fractionγP of γtot in mNm−1
8.5
D
(
0,1
) in μm
7.2
D
(
0,5
) in μm
75.6
D
(
0,9
) in μm
167.8
D
(
max
⁡
) in μm
301.6
Glass transition temperatureTg in °C
120


## 3. Materials and Methods

### 3.1. Atmospheric Pressure Plasma Layer Deposition

In order to synthesise composite PMMA/ATH, both thin and thick films on wood were realised by a thermokinetic coating technique. For this purpose, a customised plasma coating system was used. The entire setup comprises a commercially available plasma power supply and plasma generator Plasmabrush from Reinhausen Plasma GmbH with an optimised spraying nozzle and an aerosol generator as shown in Figure2. Within the system, plasma process gases are ionised and form a low temperature plasma jet. Concretely, the ignition voltage is approximately 15 kV and the effective voltage is in the range of 2-3 kV. The pulse duration amounts to 5–10 μs, where the pulse repetition rate is 50 kHz. Due to the transient nature of the discharge and a low current density, the plasma exhibits moderate temperatures at the exit of the nozzle that furthermore strongly decline along the direction of the gas flow. Depending on the plasma power (the maximum input power is 2 kW), the kind of gas, the total gas throughput (i.e., the plasma process gas and the dispersion carrier gas), and the gas velocity, typical effluent temperatures range from 100 to 200°C at a working distance of 10 mm.Figure 2
Setup of the used plasma coating system.Since the starting material was dry PMMA/ATH powder, the implemented aerosol generator was used to dose, disperse, and inject particles into the plasma jet. The powder was sieved previously so that only particles with an initial diameter <63μm were deposited. 4 mm thick beech wood samples (Fagus sylvatica L.) were used as substrates and placed on a xy-linear stage, where the lateral sample dimension was 76 × 26 mm2. Compressed air (CA) was used as process gas and as carrier gas for the particles. The process gas flow rate and the velocity of the substrate displacement were kept constant at 30 L/min and 20 mm/s, respectively. Different PMMA/ATH layers were deposited by varying the working distance, powder feed rate, and carrier gas pressure as listed in Table 2.Table 2
Parameter sets for atmospheric pressure plasma deposition of different PMMA/ATH layers.
Sample number
Working distance in mm
Powder feed rate in cm3/h
Carrier gas pressure in bar
A
15
10
2
B
13
18.1
1.5
C
13
18.1
2


### 3.2. X-Ray Photoelectron Spectroscopic (XPS) Analysis of Chemical Composition

In order to determine the chemical composition of deposited PMMA/ATH coatings, X-ray photoelectron spectroscopy (XPS) was carried out at room temperature with a base pressure of 5 × 10−8 Pa using a PHI 5000 VersaProbe II system from ULVAC-PHI. The sample surface was irradiated with an X-ray spot of 200 μm in diameter, consisting of monochromatised X-ray photons (1486.8 eV with 0.26 eV FWHM), originating from the Al Kα line. Photoelectrons emitted from the sample surface were recorded via a spherical capacitor analyser. The resulting spectra were then displayed as binding energy-dependent electron intensities, where the binding energy is given with respect to the Fermi level. Broadening effects within the system add up to a total energy resolution of <0.5 eV (FWHM Ag3d5/2). All spectra were recorded in constant energy mode at a pass energy of 23.5 eV with a step size of 0.1 eV. During the measurement, charging effects were compensated via an electron flood gun (<1 eV), running simultaneously with a low-energy (10 eV) Ar+-gun.The spectral deconvolution was carried out using the evaluation software MultiPak, where charge referencing was done by means of carbon at 284.8 eV. For quantitative analysis, sensitivity factors with correction for the analyser work function (corrected RSF) were applied after Shirley-type background correction. For the peak fitting procedure, Voigt profiles with a Lorentzian contribution of 0–22% were used in order to achieve the best agreement between experimental data and the mathematical fit. For the quantitative analysis, a total error, that is, a superposition of both the measurement and the fitting error, of 5% was assumed.


### 3.3. Confocal Laser Scanning Microscopic (CLSM) Analysis of Topography

For the investigation of the surface topography of the deposited PMMA/ATH layers, confocal laser scanning microscopy (CLSM) was performed using a Keyence VK-X210 microscope with a VK-X200K controller. The wavelength of the laser used for illumination amounts to 408 nm. The CLSM’s total magnificationmtot can be set up by varying the objective lenses (mol = 10x, 20x, 50x, and 150x) and applying the microscope’s internal magnification (10x), an 8x optical zoom, and further digital magnification. The possible total magnification then amounts to 200x to 24,000x. The images shown in this contribution were recorded using objectives with a magnification of 10x (NA = 0.3) or 150x (NA = 0.95), with all of them being superpositions of widefield microscopic and laser intensity measurements.


### 3.4. Determination of Water Contact Angle (WCA)

Water contact angle (WCA) measurements on the PMMA/ATH-coated beech samples were performed by using a commercial measuring system G10 from Krüss GmbH, where each sample was measured three times. For this purpose, a droplet (11μL) of distilled water was applied to the surface and recorded for 10 s (25 frames/sec). For every frame, the contact angle was determined by fitting a circular arc to the droplet and calculating the angle between the solid and the tangent at the point of intersection.


## 3.1. Atmospheric Pressure Plasma Layer Deposition

In order to synthesise composite PMMA/ATH, both thin and thick films on wood were realised by a thermokinetic coating technique. For this purpose, a customised plasma coating system was used. The entire setup comprises a commercially available plasma power supply and plasma generator Plasmabrush from Reinhausen Plasma GmbH with an optimised spraying nozzle and an aerosol generator as shown in Figure2. Within the system, plasma process gases are ionised and form a low temperature plasma jet. Concretely, the ignition voltage is approximately 15 kV and the effective voltage is in the range of 2-3 kV. The pulse duration amounts to 5–10 μs, where the pulse repetition rate is 50 kHz. Due to the transient nature of the discharge and a low current density, the plasma exhibits moderate temperatures at the exit of the nozzle that furthermore strongly decline along the direction of the gas flow. Depending on the plasma power (the maximum input power is 2 kW), the kind of gas, the total gas throughput (i.e., the plasma process gas and the dispersion carrier gas), and the gas velocity, typical effluent temperatures range from 100 to 200°C at a working distance of 10 mm.Figure 2
Setup of the used plasma coating system.Since the starting material was dry PMMA/ATH powder, the implemented aerosol generator was used to dose, disperse, and inject particles into the plasma jet. The powder was sieved previously so that only particles with an initial diameter <63μm were deposited. 4 mm thick beech wood samples (Fagus sylvatica L.) were used as substrates and placed on a xy-linear stage, where the lateral sample dimension was 76 × 26 mm2. Compressed air (CA) was used as process gas and as carrier gas for the particles. The process gas flow rate and the velocity of the substrate displacement were kept constant at 30 L/min and 20 mm/s, respectively. Different PMMA/ATH layers were deposited by varying the working distance, powder feed rate, and carrier gas pressure as listed in Table 2.Table 2
Parameter sets for atmospheric pressure plasma deposition of different PMMA/ATH layers.
Sample number
Working distance in mm
Powder feed rate in cm3/h
Carrier gas pressure in bar
A
15
10
2
B
13
18.1
1.5
C
13
18.1
2


## 3.2. X-Ray Photoelectron Spectroscopic (XPS) Analysis of Chemical Composition

In order to determine the chemical composition of deposited PMMA/ATH coatings, X-ray photoelectron spectroscopy (XPS) was carried out at room temperature with a base pressure of 5 × 10−8 Pa using a PHI 5000 VersaProbe II system from ULVAC-PHI. The sample surface was irradiated with an X-ray spot of 200 μm in diameter, consisting of monochromatised X-ray photons (1486.8 eV with 0.26 eV FWHM), originating from the Al Kα line. Photoelectrons emitted from the sample surface were recorded via a spherical capacitor analyser. The resulting spectra were then displayed as binding energy-dependent electron intensities, where the binding energy is given with respect to the Fermi level. Broadening effects within the system add up to a total energy resolution of <0.5 eV (FWHM Ag3d5/2). All spectra were recorded in constant energy mode at a pass energy of 23.5 eV with a step size of 0.1 eV. During the measurement, charging effects were compensated via an electron flood gun (<1 eV), running simultaneously with a low-energy (10 eV) Ar+-gun.The spectral deconvolution was carried out using the evaluation software MultiPak, where charge referencing was done by means of carbon at 284.8 eV. For quantitative analysis, sensitivity factors with correction for the analyser work function (corrected RSF) were applied after Shirley-type background correction. For the peak fitting procedure, Voigt profiles with a Lorentzian contribution of 0–22% were used in order to achieve the best agreement between experimental data and the mathematical fit. For the quantitative analysis, a total error, that is, a superposition of both the measurement and the fitting error, of 5% was assumed.


## 3.3. Confocal Laser Scanning Microscopic (CLSM) Analysis of Topography

For the investigation of the surface topography of the deposited PMMA/ATH layers, confocal laser scanning microscopy (CLSM) was performed using a Keyence VK-X210 microscope with a VK-X200K controller. The wavelength of the laser used for illumination amounts to 408 nm. The CLSM’s total magnificationmtot can be set up by varying the objective lenses (mol = 10x, 20x, 50x, and 150x) and applying the microscope’s internal magnification (10x), an 8x optical zoom, and further digital magnification. The possible total magnification then amounts to 200x to 24,000x. The images shown in this contribution were recorded using objectives with a magnification of 10x (NA = 0.3) or 150x (NA = 0.95), with all of them being superpositions of widefield microscopic and laser intensity measurements.


## 3.4. Determination of Water Contact Angle (WCA)

Water contact angle (WCA) measurements on the PMMA/ATH-coated beech samples were performed by using a commercial measuring system G10 from Krüss GmbH, where each sample was measured three times. For this purpose, a droplet (11μL) of distilled water was applied to the surface and recorded for 10 s (25 frames/sec). For every frame, the contact angle was determined by fitting a circular arc to the droplet and calculating the angle between the solid and the tangent at the point of intersection.


## 4. Results and Discussion

### 4.1. Chemical Composition of Untreated and Deposited PMMA/ATH

The XPS detail spectra before background subtraction of the O1s, Al2p, and C1s peaks for both untreated powder before deposition and thick powder coating on a beech substrate (sample B) are shown in Figure3.Figure 3
XPS detail spectra of untreated powder before deposition (solid line) and thick powder coating (dashed line). (a) O1s peak, (b) Al2p peak, and (c) C1s peak.
(a)
(b)
(c)It turns out that the Al2p peak intensity increases significantly after the deposition process. Consistently, the O1s peak is slightly shifted towards lower binding energies. This indicates a decrease of carbon-bound oxygen resulting from PMMA, where the O1s peaks are found at 532.01 eV and 533.57 eV, respectively [32]. Apparently, this comes along with an increase of aluminium-bound oxygen, where the O1s peak is located at a binding energy of 531.8 eV [33].In order to investigate whether the increase in aluminium is due to a decomposition of PMMA, the C1s peaks represented in Figure3(c) before and after the coating procedure were analysed in more detail as shown in Figure 4.Figure 4
Measured C1s peaks of (a) untreated powder before deposition and (b) thick powder coating (dotted lines) including fits (dashed lines) for particular bonds and cumulative fit (solid lines).
(a)
(b)For this purpose, the distances of the three minor fit peaks were constrained to 0.72 eV, 1.79 eV, and 4.03 eV, respectively, to the main peak. This main peak represents the peak of lowest binding energy, hereinafter referred to as MP [32]. Moreover, the ratio of the MP’s area (–CH2, –CH3) and that of the neighbouring peak (C–C4) were set to 0.5 [32]. Since the plasma coating procedure is expected to induce oxidation processes, the ratios of the peak areas corresponding to carbon atoms bound to oxygen are left unconstrained. The chemical compositions obtained by such spectral dissecting of the C1s peaks of the investigated surfaces, that is, untreated powder before deposition and thick powder coating, are summarised in Tables 3 and 4.Table 3
Binding energies (BE) of relevant peaks, particular concentrationcx, and measured relative area Ameas of carbon bonds within the C1s peak as well as literature values for Alit of the untreated powder before deposition.
Peak
BE in eV
c in at.%
A
m
e
a
s in %
A
l
i
t in % [32]
O1s
532.0
37.6
Al2p
74.4
7.2
C1s
–CH2, –CH3
284.7
22.7
41.2 (=: MPA1)
42.0 (=: MPA)
C–C4
285.5
11.4
20.6 (= 0.5 · MPA)
21.0 (= 0.5 · MPA)
–O–CH3
286.5
11.9
21.5 (= 0.5 · MPA)
21.0 (= 0.5 · MPA)
O–C=O
288.8
9.3
16.8 (= 0.4 · MPA)
17.0 (= 0.4 · MPA)
1MPA = main peak area.Table 4
Binding energies (BE) of relevant peaks, particular concentrationcx, and measured relative area Ameas of carbon bonds within the C1s peak of thick powder coating.
Peak
BE in eV
c in at.%
A
m
e
a
s in %
O1s
531.94
50.5
Al2p
74.30
15.6
C1s
–CH2, –CH3
284.78
13.8 (=: MPA)
40.6 (=: MPA)
C–C4
285.50
6.9 (=0.5 · MPA)
20.3 (= 0.5 · MPA)
–O–CH3
286.57
6.4 (= 0.46 · MPA)
18.9 (= 0.46 · MPA)
O–C=O
288.81
6.9 (= 0.50 · MPA)
20.2 (= 0.5 · MPA)As already shown in Figure3(b), the amount of aluminium increases in the course of the deposition process whereas the total carbon content decreases. Furthermore, an oxidation process takes place yielding an increased relative amount of carbon as O–C=O compound (carboxy groups). For untreated powder, the resulting ratios of the main C1s peak’s area and the other C1s peak areas are in good agreement with literature [32] as also shown in Table 3. As reported in the literature, the relative amount of methoxy groups is reduced while carboxy groups are increased but to far less extent. Hence, the arc discharge plasma used for the coating process in the present work disposes less oxidative species than the dielectric barrier discharge which was applied. In contrast to that, the resulting coatings exhibit an increased content of aluminium by a factor of about 2.2. Therefore, PMMA seems to be etched, which was also reported in [21] (cf. Introduction), and aluminium compounds are uncovered during the coating process whereas, apparently, the chemical composition of PMMA is not significantly modified. This is also confirmed by the ratios of the particular concentrations obtained from each considered peak after and before the plasma coating process cc/cp. Here, cc is the concentration of plasma-deposited material and cp is the concentration of the untreated powder corresponding to the values given in Tables 3 and 4. Figure 5 shows a radar chart of the investigated peak ratios cc/cp. On the one hand, the data in Figure 5(a) confirm the decrease in carbon, the increase in aluminium, and the oxidation of the powder. On the other hand, Figure 5(b) reveals that, irrespective of an increase of carboxy groups, the composition of the C1s peak is not significantly changed by the plasma coating process.Figure 5
Radar chart of the ratios of particular concentrations obtained from each considered peak after and before the plasma coating processcc/cp.
(a)
(b)The uncovered aluminium compounds are expected to feature a better ability to develop chemical bonds, for example, with waterborne adhesives, than the original material with a surface mainly composed of PMMA. This is also indicated by the wettability behaviour of deposited PMMA/ATH coatings as discussed hereafter in Section4.3.


### 4.2. Topography

The CLSM images of a thin plasma coating on beech wood in Figure6(a) (top and middle image) consist of superimposed widefield microscopic and laser intensity measurements. The sample is partially covered with patches of the composite polymer material while still large areas of the substrate are exposed as shown in the top image. The bottom images display the height profile along the green line within the top image. The height of these patches amounts to about 20 μm according to several of these CLSM line scans. The root means square (RMS) surface roughness RRMS amounts to 12.5 μm for the overall area shown in the top left image. On top of the white patches, the roughness evaluation yields values of 5–8 μm, while the uncovered substrate areas exhibit a RMS roughness of approximately 3 μm. A magnified detail picture of one of the white patches is additionally shown in the middle, revealing it to be roughly structured from differently sized particles.Figure 6
(a) CLSM images of a thin plasma coating on a beech wood substrate (sample A) at optical magnifications of 100x (top) and 1500x (middle) as well as a height profile along the green line within the top image. (b) CLSM images of a thick plasma coating on a beech wood substrate (sample C) at optical magnifications of 100x (top) and 1500x (middle) as well as a height profile along the green line within the top image.
(a)
(b)Figure6(b) shows images of a thick PMMA/ATH coating on beech wood as superimposed widefield microscopic images (top and middle) as well as a line profile (bottom image) along the green line within the top image. As visible in the top image, the surface is completely covered with the deposited composite polymer material. The red spots are due to residuals from differently coloured powder of the same base material. The magnified detail picture (middle) reveals a rough structure with differently sized, separate particles just as for the partially coated sample. The bottom image depicts the height profile along the green line within the top image. This line scan shows elevations with diameters of around 100 μm and heights of approximately 30–100 μm, which are not correlated with the structure of the underlying beech wood substrate. The RMS roughness amounts to RRMS=25.2 μm, thus encouraging the visual impression of a heavily ragged coating.The presence of separate particles within both coatings is rather surprising, since the glass transition temperature of the PMMA/ATH powder was determined to be about 120°C. The gas temperatures within the active region of the plasma device usually exceed 1000°C, while the remote plasma mostly exceeds the given glass transition temperature, even at a distance of 10 mm from the plasma jet nozzle (cf. Section3.1). Considering the retention time of the particles within the hot gas stream, the particle temperatures should well exceed the glass transition temperature, too, and thus the deformation of the particles as well as the mobility of the polymer chains should be large enough to assure an interdiffusion of the polymer chains and thereby the film formation process. However, the particles obviously did largely neither deform in shape nor form a closed film. Even though this should happen even for slightly cross-linked polymers, further experiments showed that, at temperatures as high as 200°C, no interdiffusion takes place for the used PMMA/ATH composite material. This might most likely be due to the chemical bonds between the PMMA and the ATH via the used functional silane-based surfactant. These findings also fit very well to the high temperature resistance of PMMA and the nearly temperature-independent modulus of elasticity up to thermal decomposition of the polymer [34]. Furthermore, there might be an influence due to the effects of the plasma treatment beyond the heat transfer, for example, the etching of the PMMA polymer. A significant formation of cross-links can be excluded from the XPS results since, here, no notable changes in the bonding structure of the carbon compounds could be determined (cf. Figures 4 and 5). Even though there is still a significant amount of PMMA left after the plasma treatment, the assumed polymer etching leads to a considerably increased fraction of the filler particles as compared to the polymer matrix (cf. Section 4.1). Thus, the glass transition temperature should further increase [31]. The main etching mechanism is the generation of short, volatile oligomers via chain scission [35], which might possibly also lead to the formation of residual short-chained oligomers at the particle surfaces. The interdiffusion and film formation processes, however, depend strongly on the interface between the PMMA/ATH particles and might therefore be significantly hindered by an adlayer of short-chained oligomers.


### 4.3. Wettability

The evolution of the water contact angles versus time is represented in Figure7. For each time interval, the average of the three measurements was plotted. As a cut-off, the shortest time of complete soaking was used. This point in time represents the limit of measurability which is found at a water contact angle of <5°. Each droplet was completely soaked by the material within the measuring period of 10 s, illustrating a high wettability of the plasma-deposited PMMA/ATH coatings. Generally, the contact angles for the thin coating (Figure 7(a), cf. also Figure 6(a)) are smaller than for the thick coatings (Figures 7(b) and 7(c), cf. also Figure 6(b)) for all time intervals. This is supposed to be caused by a surface activation of the substrate itself, that is, beech wood, as already reported, for example, by Wolkenhauer and coworkers [36].Figure 7
Evolution of the water contact angles for (a) thin coating (sample A) and thick coatings: (b) sample B, (c) sample C.
(a)
(b)
(c)In the literature, contact angles for untreated plates were found to be >60° and no soaking process was observed. The raw material is thus rather hydrophobic which is generally also valid for pure PMMA. This behaviour is confirmed by the measurements of the constant wetting rate angle on pressed powder pellets before plasma deposition (cf. Section2.1). Even though a quantitative comparison of the wettability of the PMMA/ATH plates, untreated powder, and the deposited coatings is not possible (which is due to the completely different forms, either in powder form or in solid matter), the highly hydrophilic characteristics of all plasma coatings obviously have to be correlated with a significantly increased polar part of the surface energies. Moreover, diiodomethane droplets (8 μL) were applied to study the wettability of the coatings with a nonpolar liquid, but all droplets were soaked almost immediately without yielding measurable contact angles. Hence, the resulting coatings also exhibit highly lipophilic characteristics similar to the starting material.The improved wettability is in good agreement with the results obtained by XPS. As a result of an uncovering of aluminium compounds, the wettability is enhanced by providing new bonding sites. Furthermore, the rough structure of the surface confirmed by CLSM measurements also supports this effect. In contrast to the literature, the PMMA polymer matrix of the deposited layers is not oxidised by the attachment of polar groups at all, which could contribute to the wettability with water.


## 4.1. Chemical Composition of Untreated and Deposited PMMA/ATH

The XPS detail spectra before background subtraction of the O1s, Al2p, and C1s peaks for both untreated powder before deposition and thick powder coating on a beech substrate (sample B) are shown in Figure3.Figure 3
XPS detail spectra of untreated powder before deposition (solid line) and thick powder coating (dashed line). (a) O1s peak, (b) Al2p peak, and (c) C1s peak.
(a)
(b)
(c)It turns out that the Al2p peak intensity increases significantly after the deposition process. Consistently, the O1s peak is slightly shifted towards lower binding energies. This indicates a decrease of carbon-bound oxygen resulting from PMMA, where the O1s peaks are found at 532.01 eV and 533.57 eV, respectively [32]. Apparently, this comes along with an increase of aluminium-bound oxygen, where the O1s peak is located at a binding energy of 531.8 eV [33].In order to investigate whether the increase in aluminium is due to a decomposition of PMMA, the C1s peaks represented in Figure3(c) before and after the coating procedure were analysed in more detail as shown in Figure 4.Figure 4
Measured C1s peaks of (a) untreated powder before deposition and (b) thick powder coating (dotted lines) including fits (dashed lines) for particular bonds and cumulative fit (solid lines).
(a)
(b)For this purpose, the distances of the three minor fit peaks were constrained to 0.72 eV, 1.79 eV, and 4.03 eV, respectively, to the main peak. This main peak represents the peak of lowest binding energy, hereinafter referred to as MP [32]. Moreover, the ratio of the MP’s area (–CH2, –CH3) and that of the neighbouring peak (C–C4) were set to 0.5 [32]. Since the plasma coating procedure is expected to induce oxidation processes, the ratios of the peak areas corresponding to carbon atoms bound to oxygen are left unconstrained. The chemical compositions obtained by such spectral dissecting of the C1s peaks of the investigated surfaces, that is, untreated powder before deposition and thick powder coating, are summarised in Tables 3 and 4.Table 3
Binding energies (BE) of relevant peaks, particular concentrationcx, and measured relative area Ameas of carbon bonds within the C1s peak as well as literature values for Alit of the untreated powder before deposition.
Peak
BE in eV
c in at.%
A
m
e
a
s in %
A
l
i
t in % [32]
O1s
532.0
37.6
Al2p
74.4
7.2
C1s
–CH2, –CH3
284.7
22.7
41.2 (=: MPA1)
42.0 (=: MPA)
C–C4
285.5
11.4
20.6 (= 0.5 · MPA)
21.0 (= 0.5 · MPA)
–O–CH3
286.5
11.9
21.5 (= 0.5 · MPA)
21.0 (= 0.5 · MPA)
O–C=O
288.8
9.3
16.8 (= 0.4 · MPA)
17.0 (= 0.4 · MPA)
1MPA = main peak area.Table 4
Binding energies (BE) of relevant peaks, particular concentrationcx, and measured relative area Ameas of carbon bonds within the C1s peak of thick powder coating.
Peak
BE in eV
c in at.%
A
m
e
a
s in %
O1s
531.94
50.5
Al2p
74.30
15.6
C1s
–CH2, –CH3
284.78
13.8 (=: MPA)
40.6 (=: MPA)
C–C4
285.50
6.9 (=0.5 · MPA)
20.3 (= 0.5 · MPA)
–O–CH3
286.57
6.4 (= 0.46 · MPA)
18.9 (= 0.46 · MPA)
O–C=O
288.81
6.9 (= 0.50 · MPA)
20.2 (= 0.5 · MPA)As already shown in Figure3(b), the amount of aluminium increases in the course of the deposition process whereas the total carbon content decreases. Furthermore, an oxidation process takes place yielding an increased relative amount of carbon as O–C=O compound (carboxy groups). For untreated powder, the resulting ratios of the main C1s peak’s area and the other C1s peak areas are in good agreement with literature [32] as also shown in Table 3. As reported in the literature, the relative amount of methoxy groups is reduced while carboxy groups are increased but to far less extent. Hence, the arc discharge plasma used for the coating process in the present work disposes less oxidative species than the dielectric barrier discharge which was applied. In contrast to that, the resulting coatings exhibit an increased content of aluminium by a factor of about 2.2. Therefore, PMMA seems to be etched, which was also reported in [21] (cf. Introduction), and aluminium compounds are uncovered during the coating process whereas, apparently, the chemical composition of PMMA is not significantly modified. This is also confirmed by the ratios of the particular concentrations obtained from each considered peak after and before the plasma coating process cc/cp. Here, cc is the concentration of plasma-deposited material and cp is the concentration of the untreated powder corresponding to the values given in Tables 3 and 4. Figure 5 shows a radar chart of the investigated peak ratios cc/cp. On the one hand, the data in Figure 5(a) confirm the decrease in carbon, the increase in aluminium, and the oxidation of the powder. On the other hand, Figure 5(b) reveals that, irrespective of an increase of carboxy groups, the composition of the C1s peak is not significantly changed by the plasma coating process.Figure 5
Radar chart of the ratios of particular concentrations obtained from each considered peak after and before the plasma coating processcc/cp.
(a)
(b)The uncovered aluminium compounds are expected to feature a better ability to develop chemical bonds, for example, with waterborne adhesives, than the original material with a surface mainly composed of PMMA. This is also indicated by the wettability behaviour of deposited PMMA/ATH coatings as discussed hereafter in Section4.3.


## 4.2. Topography

The CLSM images of a thin plasma coating on beech wood in Figure6(a) (top and middle image) consist of superimposed widefield microscopic and laser intensity measurements. The sample is partially covered with patches of the composite polymer material while still large areas of the substrate are exposed as shown in the top image. The bottom images display the height profile along the green line within the top image. The height of these patches amounts to about 20 μm according to several of these CLSM line scans. The root means square (RMS) surface roughness RRMS amounts to 12.5 μm for the overall area shown in the top left image. On top of the white patches, the roughness evaluation yields values of 5–8 μm, while the uncovered substrate areas exhibit a RMS roughness of approximately 3 μm. A magnified detail picture of one of the white patches is additionally shown in the middle, revealing it to be roughly structured from differently sized particles.Figure 6
(a) CLSM images of a thin plasma coating on a beech wood substrate (sample A) at optical magnifications of 100x (top) and 1500x (middle) as well as a height profile along the green line within the top image. (b) CLSM images of a thick plasma coating on a beech wood substrate (sample C) at optical magnifications of 100x (top) and 1500x (middle) as well as a height profile along the green line within the top image.
(a)
(b)Figure6(b) shows images of a thick PMMA/ATH coating on beech wood as superimposed widefield microscopic images (top and middle) as well as a line profile (bottom image) along the green line within the top image. As visible in the top image, the surface is completely covered with the deposited composite polymer material. The red spots are due to residuals from differently coloured powder of the same base material. The magnified detail picture (middle) reveals a rough structure with differently sized, separate particles just as for the partially coated sample. The bottom image depicts the height profile along the green line within the top image. This line scan shows elevations with diameters of around 100 μm and heights of approximately 30–100 μm, which are not correlated with the structure of the underlying beech wood substrate. The RMS roughness amounts to RRMS=25.2 μm, thus encouraging the visual impression of a heavily ragged coating.The presence of separate particles within both coatings is rather surprising, since the glass transition temperature of the PMMA/ATH powder was determined to be about 120°C. The gas temperatures within the active region of the plasma device usually exceed 1000°C, while the remote plasma mostly exceeds the given glass transition temperature, even at a distance of 10 mm from the plasma jet nozzle (cf. Section3.1). Considering the retention time of the particles within the hot gas stream, the particle temperatures should well exceed the glass transition temperature, too, and thus the deformation of the particles as well as the mobility of the polymer chains should be large enough to assure an interdiffusion of the polymer chains and thereby the film formation process. However, the particles obviously did largely neither deform in shape nor form a closed film. Even though this should happen even for slightly cross-linked polymers, further experiments showed that, at temperatures as high as 200°C, no interdiffusion takes place for the used PMMA/ATH composite material. This might most likely be due to the chemical bonds between the PMMA and the ATH via the used functional silane-based surfactant. These findings also fit very well to the high temperature resistance of PMMA and the nearly temperature-independent modulus of elasticity up to thermal decomposition of the polymer [34]. Furthermore, there might be an influence due to the effects of the plasma treatment beyond the heat transfer, for example, the etching of the PMMA polymer. A significant formation of cross-links can be excluded from the XPS results since, here, no notable changes in the bonding structure of the carbon compounds could be determined (cf. Figures 4 and 5). Even though there is still a significant amount of PMMA left after the plasma treatment, the assumed polymer etching leads to a considerably increased fraction of the filler particles as compared to the polymer matrix (cf. Section 4.1). Thus, the glass transition temperature should further increase [31]. The main etching mechanism is the generation of short, volatile oligomers via chain scission [35], which might possibly also lead to the formation of residual short-chained oligomers at the particle surfaces. The interdiffusion and film formation processes, however, depend strongly on the interface between the PMMA/ATH particles and might therefore be significantly hindered by an adlayer of short-chained oligomers.


## 4.3. Wettability

The evolution of the water contact angles versus time is represented in Figure7. For each time interval, the average of the three measurements was plotted. As a cut-off, the shortest time of complete soaking was used. This point in time represents the limit of measurability which is found at a water contact angle of <5°. Each droplet was completely soaked by the material within the measuring period of 10 s, illustrating a high wettability of the plasma-deposited PMMA/ATH coatings. Generally, the contact angles for the thin coating (Figure 7(a), cf. also Figure 6(a)) are smaller than for the thick coatings (Figures 7(b) and 7(c), cf. also Figure 6(b)) for all time intervals. This is supposed to be caused by a surface activation of the substrate itself, that is, beech wood, as already reported, for example, by Wolkenhauer and coworkers [36].Figure 7
Evolution of the water contact angles for (a) thin coating (sample A) and thick coatings: (b) sample B, (c) sample C.
(a)
(b)
(c)In the literature, contact angles for untreated plates were found to be >60° and no soaking process was observed. The raw material is thus rather hydrophobic which is generally also valid for pure PMMA. This behaviour is confirmed by the measurements of the constant wetting rate angle on pressed powder pellets before plasma deposition (cf. Section2.1). Even though a quantitative comparison of the wettability of the PMMA/ATH plates, untreated powder, and the deposited coatings is not possible (which is due to the completely different forms, either in powder form or in solid matter), the highly hydrophilic characteristics of all plasma coatings obviously have to be correlated with a significantly increased polar part of the surface energies. Moreover, diiodomethane droplets (8 μL) were applied to study the wettability of the coatings with a nonpolar liquid, but all droplets were soaked almost immediately without yielding measurable contact angles. Hence, the resulting coatings also exhibit highly lipophilic characteristics similar to the starting material.The improved wettability is in good agreement with the results obtained by XPS. As a result of an uncovering of aluminium compounds, the wettability is enhanced by providing new bonding sites. Furthermore, the rough structure of the surface confirmed by CLSM measurements also supports this effect. In contrast to the literature, the PMMA polymer matrix of the deposited layers is not oxidised by the attachment of polar groups at all, which could contribute to the wettability with water.


## 5. Summary and Outlook

In this work, it was shown that PMMA/ATH raw material and plasma-deposited PMMA/ATH feature notably different material properties. As a main aspect, the XPS investigations suggest that ATH was uncovered by a plasma-induced etching of the PMMA matrix in the course of the plasma deposition process as visualised in Figure8.Figure 8
Visualisation of the plasma-induced modification of PMMA/ATH by atmospheric pressure plasma powder deposition.However, based on the given results, it cannot be stated whether the ATH particles are chemically influenced by the plasma process, too, or remain as aluminium hydroxide. A more detailed investigation using Auger electron spectroscopy is planned to be carried out in ongoing work. In any case, the supplementary water contact angle measurements support an uncovering of aluminium-based bonds. In contrast to the raw material which shows a hydrophobic behaviour, the deposited coatings are rather amphiphilic. As a result of this property, the surface energy could not be determined since the analysis of contact angles of dispersed liquids was not possible. It was shown that such high wettability is not caused by the formation of additional polar groups, that is, an activation of PMMA, but most likely due to the above-mentioned uncovering of ATH. The observed decrease in carbon, giving rise to such uncovering, is most probably due to a chain scission mechanism from the plasma as described, for example, by Kuzuya and coworkers [35]. Subsequently, the resulting short-chained oligomers would desorb from the PMMA/ATH particles’ surfaces. An adjacent oxidation of these hydrocarbon molecules by the plasma towards the formation of CO2 and water is likely but has not been investigated yet.As shown by CLSM, the plasma deposition does not result in film formation. Thus, completed coatings cannot be realised by simply applying this approach. However, the uncovering of ATH provides further docking points that might improve the adhesion of glues or lacquers. In future projects, the realised coatings could thus be finished by applying either solvent- or water-based lacquers while a complete impregnation of the PMMA/ATH primary coating should be ensured due to its high wettability for polar and nonpolar liquids. In such a multicomposite system, the ATH particles could significantly improve the mechanical properties of the coating as commonly known for inorganic filler particles within polymers [8–10]. Furthermore, the ATH particles should significantly promote the adhesion between both a polar top coat matrix and the PMMA particles, due to form closure as well as due to the ATH particles being chemically bonded to the finish coating and via silane-based surfactants to the PMMA. Another finishing procedure could include a polymerization of further MMA monomers around the deposited coatings in order to maintain the excellent chemical stability and resistance against UV radiation of the raw material. This might even be possible by plasma polymerization via the addition of the MMA monomer (cf. [37]) to the process gas during the PMMA/ATH powder-based primary film deposition, which will be evaluated in a consecutive study. The development of such layer systems involving atmospheric pressure plasma powder deposition of PMMA/ATH could contribute to sustainable and resource-efficient coating processes since the raw material is recycled from waste, that is, abrasive dust which originates from classical manufacturing of PMMA/ATH work pieces as already mentioned in the Introduction.



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*Source: 980482-2015-08-17.xml*