Acrylic Pressure-Sensitive Adhesive Reinforced with Aluminum Nitride and Its Thermal Properties: E ﬀ ect of Surface Treatment and Particle Size

: Thermal interface materials (TIMs) are very crucial for better heat-transfer in electronics working as an interfacial connection between heat generators and heat sinks. This study is focused on the pressure-sensitive acrylic adhesive tape reinforced with micron-sized and nano-sized aluminum nitride (AlN) particles where the surface modiﬁcation of AlN particles is done using (3-Aminopropyl) triethoxysilane (3-APTES). The physicochemical analysis of the silanized AlN particles is done using FTIR spectroscopy and scanning electron microscopy (SEM). Furthermore, thermal properties along with thermal conductivity and thermal di ﬀ usion are also studied. The main outcome of this study shows that the sample containing surface-treated AlN particles exhibits better thermal conductivity than that of the samples containing µ and nano-sized of AlN due to the comparatively better interactions with the matrix.


Introduction
In modern electronic devices such as notebook PCs, electric cars, and LEDs, thermal management is a crucial issue. With the miniaturization of these modern devices, heat generation and its dissipation have become a challenging problem. Improper heat dissipation can cost the performance, reliability, and lifetime of the device [1]. Hence, thermal interface materials (TIMs) are very crucial for better heat-transfer in electronics working as an interfacial connection between heat generators and heat sinks. There are different types of TIMs used on commercial bases such as thermal grease, thermal gap pads, phase change materials, and form-in-place compounds. However, due to drawbacks like the requirement of pressure or mechanical clamping, contamination, degradation, and less adhesion, these types of TIMs are not favored commercially [2]. Contrarily, thermally conductive adhesive overcome all the problems and assure an exceptional bonding property between electrical components and heat sink, which eliminates the need for external clamping. Silicone, acryl, or epoxy-based double-sided thermal tapes are commonly used as thermally conductive adhesives. These tapes are thermally, mechanically, and environmentally more sustainable, more suitable for a variety of applications, and easy to design [3]. Along with the outstanding thermal conductivity, good adhesive strength and re-workability are desired in an ideal thermal conductive tape. Commercially, these tapes are used to attach heat sinks to PC processors, motor control processors, or telecommunication infrastructure components [4].
Acryl-based pressure sensitive adhesives (PSAs) are in demand from the industrial point of view due to their low-cost, durability, and secure processing. The resistivity toward the temperature,

Surface Treatment of AlN Particles
The surface of AlN particles was modified by the silanization method. Before silanization, the surface of AlN particles was cleaned by sonicating the particles in ethanol for 1 h, which was followed by filtering and drying at room temperature. For silanization, 5 wt.% of 3-APTES, based on the total weight of the treated AlN particles was added to a mixed solution of 190 mL of ethanol and 10 mL of water and stirred for 15 min. Furthermore, the desired amount of sonicated AlN particles was mixed into the above mixture and stirred for 6 h at a constant temperature of 70 • C. Afterward, the treated particles were filtered and washed many times, and followed by drying in an oven at 80 • C. These treated AlN particles are referred to as Si-AlN.

Synthesis of PSA/AlN Composites
PSA/AlN composites were prepared by mechanically mixing the AlN particles with the mixture of the UV sensitive PSA resin and hardener, which was cured by baking under the presence of UV light (Figure 1). For a better dispersion of AlN particles into the matrix, a combination of mechanical mixing and sonication was used. The heat generated through sonication made the resin comparatively less viscous and aided in better dispersion of AlN particles into the matrix. In addition, the bubbles were removed from the matrix using sonication that was beneficial as well. Furthermore, the reinforced resin was spread over the silicon-coated side of a transparent PET film with the help of a knife coater (Model: KP-3000 V, Suwon, Korea, Speed: 5 mm/sec) and cover with the silicon-coated side of a transparent PET film. Later, the sandwiched system with the resin in the middle was cured under a UV light for several minutes. Usually, in order to make a proper thermally conductive network, more than 30 wt. % of thermally conductive filler is used [13]. In addition, in some cases, the use of different sizes (µ and nano) of filler materials has been reported [14]. In this study, three combinations of composites were prepared that are referred to as µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA (Table 1). Filler-free PSA samples were also prepared as a reference.
Coatings 2020, 10, x FOR PEER REVIEW 3 of 11 The surface of AlN particles was modified by the silanization method. Before silanization, the surface of AlN particles was cleaned by sonicating the particles in ethanol for 1 h, which was followed by filtering and drying at room temperature. For silanization, 5 wt.% of 3-APTES, based on the total weight of the treated AlN particles was added to a mixed solution of 190 mL of ethanol and 10 mL of water and stirred for 15 min. Furthermore, the desired amount of sonicated AlN particles was mixed into the above mixture and stirred for 6 h at a constant temperature of 70 °C. Afterward, the treated particles were filtered and washed many times, and followed by drying in an oven at 80 °C. These treated AlN particles are referred to as Si-AlN.

Synthesis of PSA/AlN Composites
PSA/AlN composites were prepared by mechanically mixing the AlN particles with the mixture of the UV sensitive PSA resin and hardener, which was cured by baking under the presence of UV light (Figure 1). For a better dispersion of AlN particles into the matrix, a combination of mechanical mixing and sonication was used. The heat generated through sonication made the resin comparatively less viscous and aided in better dispersion of AlN particles into the matrix. In addition, the bubbles were removed from the matrix using sonication that was beneficial as well. Furthermore, the reinforced resin was spread over the silicon-coated side of a transparent PET film with the help of a knife coater (Model: KP-3000 V, Suwon, Korea, Speed: 5 mm/sec) and cover with the siliconcoated side of a transparent PET film. Later, the sandwiched system with the resin in the middle was cured under a UV light for several minutes. Usually, in order to make a proper thermally conductive network, more than 30 wt. % of thermally conductive filler is used [13]. In addition, in some cases, the use of different sizes (µ and nano) of filler materials has been reported [14]. In this study, three combinations of composites were prepared that are referred to as µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA (Table 1). Filler-free PSA samples were also prepared as a reference.

Characterization
Fourier transformed infrared (FTIR) spectroscopy using the Attenuated Total Reflectance (ATR) method was performed. The infrared (IR) spectra were collected in the wavenumber range of 400-4000 cm −1 . The morphology of AlN particles before and after the surface modification was compared using field-emission scanning electron microscopy (FE-SEM, Carl Zeiss, Germany). The surface and cross-sectional morphologies of PSA/AlN composites were also examined. Before analysis, the samples were coated with Pt via sputtering for better conductivity. Thermal degradation patterns and the associated weight loss were studied using thermogravimetric analysis, which was performed in the presence of nitrogen gas (10 mL/min) in the temperature range of 25 to 800 • C at a heating rate of 10 • C/min. The melting behavior of the composites was comparatively investigated using differential scanning calorimetry (DSC). On the other hand, thermal conductivity, thermal diffusivity, and specific heat were measured by employing a Hot Disk thermal constant analyzer (Hot Disk, Inc. USA) using a Kapton sensor tape meeting ISO Standard 22007-2 [15]. This technique is based upon the Transient Plane Source (TPS) method, where the probe is a spiral-shaped resistive element made of a metal foil covered with Kapton film from both sides acting as a heat source and sensor simultaneously. For analysis, this probe is sandwiched between two pieces of the test sample (same material). During heating, the spiral element via the electric current pulse, the increase in the resistance as a function of time is recorded to give thermal conductivity.

Physicochemical Properties
To confirm the successful silane-treatment on the surface of AlN particles, FTIR spectroscopy (PerkinElmer, Waltham, MA, USA) was used. Figure 2 shows the comparative spectra of non-treated AlN and Si-AlN. Since the samples were analyzed using the ATR method, the peak related to the adsorbed moisture is absent. Non-treated AlN display a broad absorption peak ranging from a 950 to 500 cm −1 wavelength (a) as well as a sharp peak at 1330 cm −1 wavelength (b) ascribed to vibrations of the Al-N bond [16]. While, in the case of Si-AlN, some additional peaks were also observed such as a broad peak from 3100 to 3400 cm −1 attributed to the -OH and -NH 2 , two peaks positioned at 2916 and 2847 cm −1 due to the alkyl groups, a peak at 1648 cm −1 related to the N-H bending belonging to -NH 2 groups, and peaks at around 1181 and 1067 cm −1 assigned to the Si-O-R groups of APTES [17]. Fourier transformed infrared (FTIR) spectroscopy using the Attenuated Total Reflectance (ATR) method was performed. The infrared (IR) spectra were collected in the wavenumber range of 400-4000 cm −1 . The morphology of AlN particles before and after the surface modification was compared using field-emission scanning electron microscopy (FE-SEM, Carl Zeiss, Germany). The surface and cross-sectional morphologies of PSA/AlN composites were also examined. Before analysis, the samples were coated with Pt via sputtering for better conductivity. Thermal degradation patterns and the associated weight loss were studied using thermogravimetric analysis, which was performed in the presence of nitrogen gas (10 mL/min) in the temperature range of 25 to 800 °C at a heating rate of 10 °C/min. The melting behavior of the composites was comparatively investigated using differential scanning calorimetry (DSC). On the other hand, thermal conductivity, thermal diffusivity, and specific heat were measured by employing a Hot Disk thermal constant analyzer (Hot Disk, Inc. USA) using a Kapton sensor tape meeting ISO Standard 22007-2 [15]. This technique is based upon the Transient Plane Source (TPS) method, where the probe is a spiral-shaped resistive element made of a metal foil covered with Kapton film from both sides acting as a heat source and sensor simultaneously. For analysis, this probe is sandwiched between two pieces of the test sample (same material). During heating, the spiral element via the electric current pulse, the increase in the resistance as a function of time is recorded to give thermal conductivity.

Physicochemical Properties
To confirm the successful silane-treatment on the surface of AlN particles, FTIR spectroscopy (PerkinElmer, Waltham, MA, USA) was used. Figure 2 shows the comparative spectra of non-treated AlN and Si-AlN. Since the samples were analyzed using the ATR method, the peak related to the adsorbed moisture is absent. Non-treated AlN display a broad absorption peak ranging from a 950 to 500 cm −1 wavelength (a) as well as a sharp peak at 1330 cm −1 wavelength (b) ascribed to vibrations of the Al-N bond [16]. While, in the case of Si-AlN, some additional peaks were also observed such as a broad peak from 3100 to 3400 cm −1 attributed to the -OH and -NH2, two peaks positioned at 2916 and 2847 cm −1 due to the alkyl groups, a peak at 1648 cm −1 related to the N-H bending belonging to -NH2 groups, and peaks at around 1181 and 1067 cm −1 assigned to the Si-O-R groups of APTES [17].  Figure 3 compares the FE-SEM images of the surface morphology of AlN particles before and after the silane treatment. As can be seen in Figure 3a, the surface of AlN particles was smoother with sharp cuts, which became rougher after silane treatment (Figure 3b). The reason behind this  Figure 3 compares the FE-SEM images of the surface morphology of AlN particles before and after the silane treatment. As can be seen in Figure 3a, the surface of AlN particles was smoother with sharp cuts, which became rougher after silane treatment (Figure 3b). The reason behind this roughness is the attachment of chemical groups presented in the coupling agent that reacted with the -OH group at the surface of AlN [18].
Coatings 2020, 10, x FOR PEER REVIEW 5 of 11 roughness is the attachment of chemical groups presented in the coupling agent that reacted with the -OH group at the surface of AlN [18]. The surface morphology of different PSA composites was compared using FE-SEM and shown in Figure 4. Figure 4a-f represent the FE-SEM images of µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA, respectively. To improve the image quality, the surface of all the samples was coated with platinum. Since the neat PSA sample has a very low thermal stability, it was not possible to take FE-SEM images. The sample started melting as soon as the electron beam was focused on it. From images, it was found that the sample µ-AlN/n-AlN/PSA shows the roughest surface as compared to the others, which indicates a great degree of agglomeration. This happened due to the lack of interactions between the non-treated particles and matrix, which was even confirmed in Figure 4b. Figure 4b is an SEM image of the edge of the sample from where it was cut. Since bare AlN particles do not have any compatible chemical functional group that can interact with the acrylate group present in the matrix that leads to poor dispersion of AlN particles into the matrix. The surface of the Si-µ-AlN/n-AlN/PSA was comparatively smoother, which indicates a proper dispersion of µ-AlN and n-AlN particles into the matrix. As can be seen from Figure 4d, the edge of the sample was smoother than the µ-AlN/n-AlN/PSA because functional groups presented on the silane-treated µ-AlN surface formed bonds with chemical groups of PSA improving the interactions between AlN particles and the matrix. During the silanization process, APTES molecules are chemosorbed onto the surface of AlN particles by forming chemical bonds of type "AlN-O-Si-" as a result of a reaction between the possible -OH groups on the AlN surface and the ethoxy moiety of APTES. In this case, it corresponds to the amounts of ethanol generated as a by-product. Afterward, the functionalized surface (with -NH2 groups) of AlN particles could strongly interact via hydrogen bonding with the PSA matrix (ester groups), which enhances the strength of adhesion between the inorganic (AlN particles) and organic (PSA matrix) phases of the mixed systems. Particles were more evenly dispersed in Si-µ-AlN/PSA as compared to the Si-µ-AlN/n-AlN/PSA because all the AlN were treated with the coupling agent that improved the dispersion and interactions between chemical groups present on the surface of AlN particles with chemical moieties of the matrix [19]. In addition, due to the absence of the non-treated n-AlN particles, a proper conducting network was formed. The FE-SEM image of the edge of the cut sample was in accordance with the SEM image of the surface. The surface morphology of different PSA composites was compared using FE-SEM and shown in Figure 4. Figure 4a-f represent the FE-SEM images of µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA, respectively. To improve the image quality, the surface of all the samples was coated with platinum. Since the neat PSA sample has a very low thermal stability, it was not possible to take FE-SEM images. The sample started melting as soon as the electron beam was focused on it. From images, it was found that the sample µ-AlN/n-AlN/PSA shows the roughest surface as compared to the others, which indicates a great degree of agglomeration. This happened due to the lack of interactions between the non-treated particles and matrix, which was even confirmed in Figure 4b. Figure 4b is an SEM image of the edge of the sample from where it was cut. Since bare AlN particles do not have any compatible chemical functional group that can interact with the acrylate group present in the matrix that leads to poor dispersion of AlN particles into the matrix. The surface of the Si-µ-AlN/n-AlN/PSA was comparatively smoother, which indicates a proper dispersion of µ-AlN and n-AlN particles into the matrix. As can be seen from Figure 4d, the edge of the sample was smoother than the µ-AlN/n-AlN/PSA because functional groups presented on the silane-treated µ-AlN surface formed bonds with chemical groups of PSA improving the interactions between AlN particles and the matrix. During the silanization process, APTES molecules are chemosorbed onto the surface of AlN particles by forming chemical bonds of type "AlN-O-Si-" as a result of a reaction between the possible -OH groups on the AlN surface and the ethoxy moiety of APTES. In this case, it corresponds to the amounts of ethanol generated as a by-product. Afterward, the functionalized surface (with -NH 2 groups) of AlN particles could strongly interact via hydrogen bonding with the PSA matrix (ester groups), which enhances the strength of adhesion between the inorganic (AlN particles) and organic (PSA matrix) phases of the mixed systems. Particles were more evenly dispersed in Si-µ-AlN/PSA as compared to the Si-µ-AlN/n-AlN/PSA because all the AlN were treated with the coupling agent that improved the dispersion and interactions between chemical groups present on the surface of AlN particles with chemical moieties of the matrix [19]. In addition, due to the absence of the non-treated n-AlN particles, a proper conducting network was formed. The FE-SEM image of the edge of the cut sample was in accordance with the SEM image of the surface.

Thermal Properties
To study the thermal behavior of the prepared samples, TGA was performed. Figure 5 displays the TGA patterns of PSA, µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA, respectively. Of all the studied systems, neat PSA exhibits the highest weight loss that means the lowest thermal stability. The TGA pattern of neat PSA shows two-steps while other samples have a three-steps degradation pattern. These two steps of degradation in neat PSA are ascribed to the degradation of polymer chains (at around 290 °C) and total decomposition of the polymer (at around 370 °C) in PSA, respectively [20]. In all the AlN reinforced PSA composites, one extra step at around 100 °C, ascribed to the adsorbed moisture on AlN particles due to their hygroscopic nature, is also observed. Table 2 indicates the observed weight loss in different steps for different samples. To compare the thermal stability, the heat-resistance index is also calculated using Equation (1) at the decomposition temperature for 5% and 30% weight loss (T5 and T30), respectively [21].

Thermal Properties
To study the thermal behavior of the prepared samples, TGA was performed. Figure 5 displays the TGA patterns of PSA, µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA, respectively. Of all the studied systems, neat PSA exhibits the highest weight loss that means the lowest thermal stability. The TGA pattern of neat PSA shows two-steps while other samples have a three-steps degradation pattern. These two steps of degradation in neat PSA are ascribed to the degradation of polymer chains (at around 290 • C) and total decomposition of the polymer (at around 370 • C) in PSA, respectively [20]. In all the AlN reinforced PSA composites, one extra step at around 100 • C, ascribed to the adsorbed moisture on AlN particles due to their hygroscopic nature, is also observed. Table 2 indicates the observed weight loss in different steps for different samples. To compare the thermal stability, the heat-resistance index is also calculated using Equation (1) at the decomposition temperature for 5% and 30% weight loss (T 5 and T 30 ), respectively [21].
As can be seen in Table 3, the heat-resistance index was improved from 157.67 (for PSA) to 202.29 (for Si-µ-AlN/PSA). The heat-resistance indexes of µ-AlN/n-AlN/PSA and Si-µ-AlN/n-AlN/PSA are very close to each other, while Si-µ-AlN/PSA exhibited the highest heat-resistance index. This could be explained as, after surface-treatment of AlN particles, the functional groups attached to the surface of the particles react with the chemical groups of the polymer matrix and create a continuous network reducing chain movements during thermal treatment [22]. Hence, the Si-µ-AlN/PSA becomes thermally more stable. On the other hand, the interfacial interactions were comparatively weak in µ-AlN/n-AlN/PSA due to the non-treated AlN particles resulting in low thermal stability. Similarly, the presence of non-treated n-AlN in Si-µ-AlN/n-AlN/PSA affected the thermal stability negatively in comparison to the Si-µ-AlN/PSA. be explained as, after surface-treatment of AlN particles, the functional groups attached to the surface of the particles react with the chemical groups of the polymer matrix and create a continuous network reducing chain movements during thermal treatment [22]. Hence, the Si-µ-AlN/PSA becomes thermally more stable. On the other hand, the interfacial interactions were comparatively weak in µ-AlN/n-AlN/PSA due to the non-treated AlN particles resulting in low thermal stability. Similarly, the presence of non-treated n-AlN in Si-µ-AlN/n-AlN/PSA affected the thermal stability negatively in comparison to the Si-µ-AlN/PSA.   Figure 6 shows the out-of-the-plane thermal conductivity measured through the Hot Disk method containing the Kapton sensor for all the analyzed samples. As can be seen from the graphs, the thermal conductivity of the neat PSA sample was too low (0.18 Wm −1 K −1 ). While, after the incorporation of AlN particles, all the samples show improved thermal conductivity. The thermal conductivity for µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA were 0.58, 0.68, and 0.75 Wm −1 K −1 , respectively, which were 222%, 277%, and 316% higher than that of neat PSA samples. The reason behind this improvement is the formation of a proper thermally conductive network of AlN in the PSA matrix. Generally, neat polymers are thermal insulators. In order to increase their thermal properties, thermally conductive fillers are mixed [23]. When these fillers are dispersed into a higher weight percentage, they form a proper thermally conductive network that helps in phonon  Table 2. Thermogravimetric analysis data of PSA, µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA.

No.
Sample Name Weight Loss (%) I II III  Table 3. Heat resistance index of PSA, µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA.  Figure 6 shows the out-of-the-plane thermal conductivity measured through the Hot Disk method containing the Kapton sensor for all the analyzed samples. As can be seen from the graphs, the thermal conductivity of the neat PSA sample was too low (0.18 Wm −1 K −1 ). While, after the incorporation of AlN particles, all the samples show improved thermal conductivity. The thermal conductivity for µ-AlN/n-AlN/PSA, Si-µ-AlN/n-AlN/PSA, and Si-µ-AlN/PSA were 0.58, 0.68, and 0.75 Wm −1 K −1 , respectively, which were 222%, 277%, and 316% higher than that of neat PSA samples. The reason behind this improvement is the formation of a proper thermally conductive network of AlN in the PSA matrix. Generally, neat polymers are thermal insulators. In order to increase their thermal properties, thermally conductive fillers are mixed [23]. When these fillers are dispersed into a higher weight percentage, they form a proper thermally conductive network that helps in phonon transfer during heat treatment [24]. Ironically, the intrinsic value of the filler material can never be attained due to the phonon scattering occurring at the interfacial surface between the filler and matrix. In addition to the weight percentage, size, dispersion, aspect ratio, and alignment of filler material also affect the thermal conductivity of the material [12]. In this study, in the case of µ-AlN/n-AlN/PSA and Si-µ-AlN/n-AlN/PSA, along with the micron-sized AlN particles, nano-sized AlN particles are also mixed. When µ-AlN is dispersed into the matrix, some voids are also generating among them. These n-AlN particles fill these gaps by maintaining a proper thermally conductive network, and, consequently, thermal conductivity increases [25]. In Si-µ-AlN/n-AlN/PSA, silanized µ-AlN was the main reason behind the increased thermal conductivity. The functional groups present on the Si-µ-AlN surface form bonds with chemical groups of PSA, which improves the interactions between AlN particles and the matrix. Hence, Si-µ-AlN/n-AlN/PSA shows a 17% increase in thermal conductivity as compared to the µ-AlN/n-AlN/PSA. Si-µ-AlN/PSA exhibits the highest thermal conductivity because improved interactions between Si-µ-AlN particles and the matrix effectively disperse the particles throughout the matrix, which forms an interconnected touching network of Si-µ-AlN particles creating an optimal thermal path through the matrix [26]. The thermal conductivity of Si-µ-AlN/PSA is 10% more than that of Si-µ-AlN/n-AlN/PSA. The probable reason behind this could be the lack of interactions between non-treated nano-sized AlN particles and matrix/Si-µ-AlN. Moreover, there are reports that say the filler material with smaller size scatters more phonons because of the higher density of interfaces acting as Kapitza resistance leading to lower conductivity (Figure 7) [27]. It can be assumed that the thermal conductivity is more influenced by interactions between filler particles than size. Hence, Si-µ-AlN/n-AlN/PSA has comparatively lower thermal conductivity than the Si-µ-AlN/PSA. transfer during heat treatment [24]. Ironically, the intrinsic value of the filler material can never be attained due to the phonon scattering occurring at the interfacial surface between the filler and matrix. In addition to the weight percentage, size, dispersion, aspect ratio, and alignment of filler material also affect the thermal conductivity of the material [12]. In this study, in the case of µ-AlN/n-AlN/PSA and Si-µ-AlN/n-AlN/PSA, along with the micron-sized AlN particles, nano-sized AlN particles are also mixed. When µ-AlN is dispersed into the matrix, some voids are also generating among them. These n-AlN particles fill these gaps by maintaining a proper thermally conductive network, and, consequently, thermal conductivity increases [25]. In Si-µ-AlN/n-AlN/PSA, silanized µ-AlN was the main reason behind the increased thermal conductivity. The functional groups present on the Si-µ-AlN surface form bonds with chemical groups of PSA, which improves the interactions between AlN particles and the matrix. Hence, Si-µ-AlN/n-AlN/PSA shows a 17% increase in thermal conductivity as compared to the µ-AlN/n-AlN/PSA. Si-µ-AlN/PSA exhibits the highest thermal conductivity because improved interactions between Si-µ-AlN particles and the matrix effectively disperse the particles throughout the matrix, which forms an interconnected touching network of Siµ-AlN particles creating an optimal thermal path through the matrix [26]. The thermal conductivity of Si-µ-AlN/PSA is 10% more than that of Si-µ-AlN/n-AlN/PSA. The probable reason behind this could be the lack of interactions between non-treated nano-sized AlN particles and matrix/Si-µ-AlN. Moreover, there are reports that say the filler material with smaller size scatters more phonons because of the higher density of interfaces acting as Kapitza resistance leading to lower conductivity ( Figure 7) [27]. It can be assumed that the thermal conductivity is more influenced by interactions between filler particles than size. Hence, Si-µ-AlN/n-AlN/PSA has comparatively lower thermal conductivity than the Si-µ-AlN/PSA.   The thermal diffusivity and specific heat capacity of all samples are also represented in Figure 6. As expected, the neat PSA sample shows the lowest thermal diffusivity and specific heat capacity in comparison to the other PSA composites. Among all PSA composites, Si-µ-AlN/n-AlN/PSA and Siµ-AlN/PSA exhibit similar thermal diffusivity, which was higher than that of the µ-AlN/n-AlN/PSA sample. This happens because a continuous phase is created where the polymer matrix is immobilized on the surface of AlN particles (Figure 7) [28]. The order of specific heat capacity for PSA composites was Si-µ-AlN/n-AlN/PSA (1.442 MJ/m³K) < PSA (1.549 MJ/m³K) < Si-µ-AlN/PSA (1.639 MJ/m³K) < µ-AlN/n-AlN/PSA (1.666 MJ/m³K). This could be explained by the improved interfacial interactions between AlN particles and the matrix. As mentioned previously, due to the silane surface-treatment of AlN particles, their dispersion as well as interfacial interaction with the matrix also improved. Hence, a continuous phase is created. Consequently, the density of all the samples differs as samples with treated AlN particles are likely to be denser due to the absence (or a lesser number) of voids and better interactions [29]. In addition, the sample containing the n-AlN could be denser due to the presence of n-AlN particles that fill the void present in the matrix, which leads toward the lower specific heat. Furthermore, in order to analyze the statistical difference of the means (for each cases) of thermal conductivity, thermal diffusivity, and specific heat, ANOVA was performed, and the significance is indicated in Figure 6.

Conclusions
In this study, the acrylic pressure-sensitive adhesive was prepared by mixing aluminum nitride particles with different sizes. To further improve the interactions between the polymer matrix and AlN particles, particles were treated with 3-APTES, which is a silane coupling agent. The presence of 3-APTES related peaks in FTIR spectra confirmed the successful attachment of chemical moieties on AlN particles. Additionally, SEM images displayed the changes in surface morphology occurred after surface treatment. Thermal conductivity data showed that improving the interfacial interaction between the acrylic matrix and AlN using a surface coupling agent exhibited better thermal conductivity than that of altering the interfacial distance by incorporating n-AlN. This happened because, after treatment, acrylic chains were more easily anchored on the surface of AlN reducing the interfacial thermal resistance while, in another case, the interfacial gap between treated AlN and non-treated n-AlN was responsible for more heat loss.  The thermal diffusivity and specific heat capacity of all samples are also represented in Figure 6. As expected, the neat PSA sample shows the lowest thermal diffusivity and specific heat capacity in comparison to the other PSA composites. Among all PSA composites, Si-µ-AlN/n-AlN/PSA and Si-µ-AlN/PSA exhibit similar thermal diffusivity, which was higher than that of the µ-AlN/n-AlN/PSA sample. This happens because a continuous phase is created where the polymer matrix is immobilized on the surface of AlN particles (Figure 7) [28]. The order of specific heat capacity for PSA composites was Si-µ-AlN/n-AlN/PSA (1.442 MJ/m 3 K) < PSA (1.549 MJ/m 3 K) < Si-µ-AlN/PSA (1.639 MJ/m 3 K) < µ-AlN/n-AlN/PSA (1.666 MJ/m 3 K). This could be explained by the improved interfacial interactions between AlN particles and the matrix. As mentioned previously, due to the silane surface-treatment of AlN particles, their dispersion as well as interfacial interaction with the matrix also improved. Hence, a continuous phase is created. Consequently, the density of all the samples differs as samples with treated AlN particles are likely to be denser due to the absence (or a lesser number) of voids and better interactions [29]. In addition, the sample containing the n-AlN could be denser due to the presence of n-AlN particles that fill the void present in the matrix, which leads toward the lower specific heat. Furthermore, in order to analyze the statistical difference of the means (for each cases) of thermal conductivity, thermal diffusivity, and specific heat, ANOVA was performed, and the significance is indicated in Figure 6.

Conclusions
In this study, the acrylic pressure-sensitive adhesive was prepared by mixing aluminum nitride particles with different sizes. To further improve the interactions between the polymer matrix and AlN particles, particles were treated with 3-APTES, which is a silane coupling agent. The presence of 3-APTES related peaks in FTIR spectra confirmed the successful attachment of chemical moieties on AlN particles. Additionally, SEM images displayed the changes in surface morphology occurred after surface treatment. Thermal conductivity data showed that improving the interfacial interaction between the acrylic matrix and AlN using a surface coupling agent exhibited better thermal conductivity than that of altering the interfacial distance by incorporating n-AlN. This happened because, after treatment, acrylic chains were more easily anchored on the surface of AlN reducing the interfacial thermal resistance while, in another case, the interfacial gap between treated AlN and non-treated n-AlN was responsible for more heat loss.