Startseite Polyarylene ether nitrile dielectric films modified by HNTs@PDA hybrids for high-temperature resistant organic electronics field
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Polyarylene ether nitrile dielectric films modified by HNTs@PDA hybrids for high-temperature resistant organic electronics field

  • Siyi Chen , Shuang Yang , Sisi Chen , Fang Zuo , Pan Wang , Ying Li und Yong You EMAIL logo
Veröffentlicht/Copyright: 8. September 2023
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Nanotechnology Reviews
Aus der Zeitschrift Nanotechnology Reviews Band 12 Heft 1

Abstract

In this work, mussel-inspired surface functionalization of halloysite nanotubes (HNTs) were coated by in situ self-polymerization of polydopamine (PDA) to synthesize core-shell structural composites (HNTs@PDA), and then incorporated into polyarylene ether nitrile (PEN) matrix. Due to the strong adhesion of the PDA modification layer and the formation of hydrogen bonds between the polar nitrile group of PEN and the catechol group of PDA, the dispersion and interfacial compatibility of HNTs@PDA in the PEN matrix are improved. The results show that the dielectric constant of PEN/HNTs@PDA 20 nanocomposites reaches 11.56 (1 kHz), which is 3.2 times that of pure PEN. In addition, after heat treatment, a chemical cross-linking reaction occurred between the PEN matrix to form a cross-linked PEN (CPEN) based nanocomposites, which further improved the thermal stability of the nanocomposites. The results show that the T g of CPEN/HNTs@PDA 20 nanocomposites reaches 215.5°C, which is 47.7°C higher than that of PEN/HNTs@PDA 20. Moreover, the dielectric constant-temperature coefficient of all CPEN nanocomposites is less than 7 × 10−4°C−1 at the temperature range of 25–180°C. All in all, this work provides a simple and environmentally friendly strategy to adjust the dielectric properties of polymer-based ceramic nanocomposites, which provides a pathway for its application as a dielectric material in the film capacitors field.

Keywords: polyarylene ether nitrile; nanocomposites; dielectric properties; core-shell structure

1 Introduction

In recent years, polymer-based nanocomposites with outstanding dielectric properties and high temperature resistance have received increasing attention due to the widespread demand in the electronic device fields [1]. Although the traditional inorganic ceramic dielectrics are widely used owing to their high dielectric constant, their inherent characteristics of heavy weight, difficult processing, and brittleness are no longer sufficient for the current practical application. In comparison, polymeric materials have exhibited the advantages of lightweight and flexibility, but their low dielectric constant also limits their application to a great extent. Therefore, combining the two-component materials is an effective way to overcome these limitations. Therefore, polymer/ceramic-filler dielectric nanocomposites have become a significant research direction for energy storage field due to its combination of high insulation, high mechanical strength, and easy processing, as well as the great high dielectric constant and stable thermal stability [2].

Nowadays, ceramic nanomaterials, such as BaTiO3 and TiO2 [3], are commonly used in the preparation of high dielectric polymer nanocomposites. Among these nanofillers, halloysite nanotubes (HNTs), consisting of a natural bilayer structure of silica-aluminate [4], is a one-dimensional tubular ceramic material with excellent mechanical strength and thermal stability. HNTs have many advantages in applications due to their structure similar to that of carbon nanotubes (CNTs) [5,6,7]. On the one hand, HNTs are abundant in source, inexpensive, non-toxic and non-hazardous, and has good biocompatibility. On the other hand, HNTs have fewer functional groups on its surface and less π–π interactions between nanotubes, enabling easier dispersion in matrix polymer resin. Consequently, HNTs offer a viable alternative to the more expensive CNTs in polymer nanocomposites and multifunctional nanocomposites.

Polyarylene ether nitrile (PEN) [8,9], as a new class of high-performance and high-temperature resistant special engineering plastics, has received wide attention for its good processing properties, outstanding thermal stability, and tensile strength. It is because of a large number of benzene rings in the backbone of the PEN molecule, which makes the molecular chain segments have high mechanical strength. The presence of the strong polar side group nitrile makes PEN have a dielectric constant between 3.8 and 6.0 [10]. Additionally, PEN exhibits high temperature and corrosion resistance, expanding its applications across various industries. However, similar to many polymers, their relatively low dielectric constants and energy storage densities make it difficult to meet the current practical applications. Despite extensive research on dielectric nanocomposites based on materials such as GO, HNTs, and BaTiO3 [11,12,13], their dielectric losses remain at elevated level. Hence, further exploration is necessary to devise high-performance polymer-based nanocomposites.

As we are aware, the interface compatibility between the matrix and the nanofiller plays a crucial role in the preparation of polymer-based nanocomposites with exceptional comprehensive properties. Inadequate interfacial compatibility can result in nanofiller aggregation within the matrix, leading to high dielectric loss. Therefore, it is essential to introduce a simple and effective method for nanoparticle surface modification needs to be introduced. Recently, dopamine (DA) has often been used by researchers as a surface modification material for nanomaterials owing to its abundant hydroxyl functional groups and good adhesion properties on its surface [14,15]. In addition, DA can also form polydopamine (PDA) by in situ self-polymerization under certain conditions [16]. It can effectively improve the interfacial compatibility.

In this work, PEN/HNTs@PDA one-dimensional nanotube composite films were designed. Initially, the HNTs were first coated with a PDA organic layer, which offers abundant surface hydroxyl groups. Subsequently, different mass fractions of HNTs@PDA were introduced into PEN for preparing PEN/HNTs@PDA nanocomposites. Finally, the dielectric, mechanical, and thermal properties of PEN/HNTs@PDA composite films are studied in detail, and the influence of interface compatibility between HNTs@PDA and PEN matrix on the structure and properties of composite films is further explored, which provides a new way for the preparation of polymer nanocomposites with excellent comprehensive properties.

2 Experimental methods

2.1 Materials

HNTs (AR) was provided from Guangzhou Worun Material Technology Co., Ltd (China); Dopamine hydrochloride (98%) was purchased from Chengdu Best Reagent Co., Ltd (China). Tris(hydroxymethyl) aminomethane (99.9%), concentrated hydrochloric acid (HCl, AR), and N-methyl-2-pyrrolidone (NMP, 98%) were purchased from Kelong Reagent Co., Ltd, Chengdu, China. The PEN was synthesized in the laboratory. All materials were used without further purification.

2.2 Preparation of PEN composite dielectric films

The core-shell structure of the PDA interface functionalized HNTs were prepared through in situ self-polymerization of DA, and the corresponding preparation mechanism diagram is shown in Figure 1. First, HNTs (0.40 g) were dispersed into Tris-HCl buffer solution (200 mL) with ultrasonic stirring. Then, dopamine hydrochloride (0.20 g) was added to the system and continued the stirring reaction for 4 h. The products were repeatedly washed with deionized water to neutral, and dried at 50°C overnight to obtain HNTs@PDA hybrids.

Figure 1 Schematic diagram of the preparation of HNTs@PDA hybrids.
Figure 1

Schematic diagram of the preparation of HNTs@PDA hybrids.

PEN was synthesized in the laboratory following the procedures outlined in the literature [17], and its structure is presented in Figure S1. The PEN nanocomposites were prepared by solution casting method. The specific steps are as follows: first, a certain mass of HNTs@PDA hybrids was placed in NMP solvent and dispersed by ultrasonic waves for 1 h, then the corresponding mass of PEN powder was added and heated at 200°C for 2 h until the PEN is completely dissolved. After that, the solution of PEN/HNTs@PDA was slowly poured onto a horizontally placed glass plate with the procedure of 80/100/120/160°C for 1 h and 200°C for 2 h, respectively. Finally, after natural cooling to room temperature, the PEN/HNTs@PDA composite film was obtained. The PEN nanocomposites with HNTs@PDA mass fractions of 0/5/10/15/20 wt%, which were named as PEN, PEN/HNTs@PDA 5, PEN/HNTs@PDA 10, PEN/HNTs@PDA 15, and PEN/HNTs@PDA 20. Additionally, the composite films with HNTs mass fraction of 5/10/15/20 wt% were prepared and named as PEN/HNTs 5, PEN/HNTs 10, PEN/HNTs 15, and PEN/HNTs 20.

The above PEN/HNTs@PDA nanocomposites were placed in a high temperature oven at 320°C for 4 h. After natural cooling, the composite films were detached from the glass plates and labeled as cross-linked PEN (CPEN), CPEN/HNTs@PDA 5, CPEN/HNTs@PDA 10, CPEN/HNTs@PDA 15, and CPEN/HNTs@PDA 20.

2.3 Characterization

Fourier-transform infrared (FTIR, Thermo Nicolet, IR 200) spectra were obtained in the attenuated total reflectance mode from 400–4,000 cm−1. The X-ray diffraction (XRD, Beijing Pu-Analysis General Instrument, XD-6, 4°/min) analysis was tested at a range of 5°–85°. UV-vis spectroscopy (UV-500, Thermo Nicolet) was tested at 200–900 nm. Zeta potential of the nanotubes was tested by using a zetasizer instrument (Nano zs, Malvern, USA). Each sample was measured three times to ensure repeatability. The microscopic morphology images were tested by SEM (JEOL JSM-5900LV, Tokyo, Japan) and TEM (JEOL JEM-F20, Tokyo, Japan). Mechanical properties were tested on electromechanical universal testing machine (QX-W200, Shanghai Qixiang Testing Instrument Co., Ltd), the tensile rate is 5 mm/min. Differential scanning calorimetry (DSC, TA, Q2000, 10°C/min) was used to investigate the change in glass transition temperature of the polymer films, which were tested in an atmosphere of N2 over a range of 50–400°C. The thermal stability of the materials was characterized by thermogravimetric analysis (TGA, TA, Q50, 20°C/min) over the range of 25–800°C. Dielectric properties were measured by a TH2819A LCR meter (Tonghui Electronics Co., Ltd, China) from 100 Hz to1 MHz. The heat transfer properties were analyzed using Infrared thermal imager (FLIR Systems Inc, NASDAQ: FLIR).

3 Results and discussion

3.1 Structural characterization of HNTs@PDA

The FTIR spectra of HNTs and HNTs@PDA are shown in Figure 2(a). Among them, the characteristic peaks observed at 3,716 and 3,635 cm−1 belongs to the stretching vibration of Al-OH, the characteristic peak at 1,037 cm−1 is mainly caused by the stretching vibration of Si–O group in HNTs. Additionally, peak at 917 cm−1 indicates the bending vibration of Al-OH and another bending vibration peak of Al–O–Si at 517 cm−1. These peaks confirm the presence of these respective groups in HNTs [18]. Besides, the peak appearing at 3,444 cm−1 on the curve of HNTs@PDA is the stretching vibration of –OH and –N–H in PDA. For the absorption peak at 1,627 cm−1, it is the peak of –N–H bending vibration in PDA. And the characteristic peaks located at 1,508 and 1,290 cm−1 are the peaks of the stretching vibration of the C–C group on the benzene ring and the characteristic absorption peak of the phenolic hydroxyl group in PDA, respectively [19,20]. Therefore, the result can prove that HNTs are successfully modified by PDA.

Figure 2 Characterization of HNTs and HNTs@PDA hybrids: (a) FTIR spectra; (b) XRD patterns; (c) UV-vis spectra; (d) TGA curves; (e) zeta potential spectra; (f) XPS survey spectra; (g) O1s, (h) C1s, and (i) N1s XPS spectra of HNTs@PDA.
Figure 2

Characterization of HNTs and HNTs@PDA hybrids: (a) FTIR spectra; (b) XRD patterns; (c) UV-vis spectra; (d) TGA curves; (e) zeta potential spectra; (f) XPS survey spectra; (g) O1s, (h) C1s, and (i) N1s XPS spectra of HNTs@PDA.

Figure 2(b) shows the XRD diffraction spectra of HNTs and HNTs@PDA. By comparing the PDF standard card (JCPDF#29-1487), it can be seen that pure HNTs have distinct diffraction peaks at 2θ = 12.1°, 20.1°, 24.6°, 35°, 54.5°, and 62.5°, which represents the presence of (001), (110), (002), (110), (210), and (300) crystal planes in its crystal structure [21]. The result indicates that the crystal structure of the HNTs did not change before and after the PDA coating. Meanwhile, as shown in Figure 2(c), the HNTs, HNTs@PDA as well as DA were tested by UV-Vis spectroscopy. The curves of DA and HNTs@PDA both have absorption peaks at about 277 nm, which are mainly the absorption of the benzene ring in the system [22]. This result proves that the PDA is successfully coated on the surface of HNTs. The amount of PDA coating on the surface of functionalized HNTs were investigated by TGA analysis. Figure 2(d) shows the TGA curves of the HNTs before and after modification. It can be seen that the weight loss of HNTs is 13.30% at 800°C, which is mainly due to the decomposition of hydroxyl functional groups (Al–OH) on the surface of HNTs. In contrast, HNTs@PDA has a larger weight loss than that of HNTs in the temperature range of 50–800°C, reaching 23.55%. From the change in weight fraction, it can be estimated that the coating amount of PDA is about 8.6%, which further confirms that the surface of HNTs is successfully coated by PDA. Zeta potential measurements reflect the amount of charge carried by the solid surface. The aqueous solutions of HNTs and HNTs@PDA were characterized by zeta potential, which are shown in Figure 2(e) [22]. It can be seen that both HNTs and HNTs@PDA are negatively charged with zeta potential values of −10.2 and −26.7 mV, respectively. The zeta potential is mainly related to the charge on the surface of the filler, and HNTs exhibit a negative charge due to the hydroxyl group on their surface. In addition, when the DA monomer forms PDA by in situ oxidative self-polymerization, a large number of catechol groups are exposed on its surface, showing a negative potential. It is once again demonstrated that PDA successfully modifies the surface of HNTs and causes a significant reduction in the zeta potential of the filler [23]. Therefore, the absolute value of the zeta potential of the HNTs@PDA is much larger than that of HNTs, and according to the principle of uniform charge mutual repulsion, the charge repulsion between the HNTs@PDA is much greater than that between the HNTs, which makes the HNTs@PDA hybrids less easy to aggregate and will be better dispersed in the polymer matrix. This result is consistent with the dispersion test of the filler in the NMP solvent.

As shown in Figure S2, the PDA-modified HNTs have excellent dispersion in the NMP solvent, and there is still no obvious agglomeration phenomenon after 48 h, while the pure HNTs settle almost completely due to agglomeration after 1 h in the NMP solvent. This result is due to the fact that a large number of catechol groups are exposed on the surface of the PDA, resulting in a significant increase in the absolute value of the zeta potential of HNTs@PDA. According to the principle of charge repulsion, the repulsion between negative charges makes HNTs@PDA hybrids less prone to agglomeration and better dispersed in NMP.

In Figure 2(f), the XPS spectra of HNTs and HNTs@PDA hybrids are displayed. The HNTs@PDA spectrum reveals a diffraction peak at 400.05 eV for N1s, primarily originating from the N element in the PDA of the HNTs@PDA hybrids [24]. Meanwhile, the O1s, C1s, and N1s of the HNTs@PDA exhibit distinctive split peaks. As depicted in Figure 2(g)–(i), the C1s spectra is fitted with three diffraction peaks at 288.50, 286.02, and 284.75 eV, corresponding to the C═O, C–N/C–OH, and C–C/C═C/C–H bonds, respectively [25]. The N1s spectra at 398.14 and 400.09 eV are fitted with two diffraction peaks corresponding to –N═ and –NH– bonds, respectively [26]. It indicates that self-polymerization reactions are performed between the DA, which is consistent with the polymerization mechanism proposed in the previous results of FTIR and TGA. It also confirms the successful preparation of PDA-modified layer on the HNTs.

The SEM images of nanofillers are shown in Figure 3. As shown in Figure 3a and b, the HNTs have a one-dimensional tubular structure with smooth outer surface and relatively uniform size. In contrast, the PDA-modified HNTs display varying sizes and rough surfaces (Figure 3c and d), providing further evidence of the attachment of the PDA layer around the HNTs.

Figure 3 SEM images of functional nanofillers: (a) and (b) HNTs; (c) and (d) HNTs@PDA.
Figure 3

SEM images of functional nanofillers: (a) and (b) HNTs; (c) and (d) HNTs@PDA.

The microstructure of HNTs and HNTs@PDA was further assessed using TEM. As shown in Figure 4a and b, the pristine HNTs were tubular with smooth surface and no obvious ripples and folds. However, following the surface modification of HNTs, the HNTs were enveloped by a thin organic layer (Figure 4c and d), providing further confirmation of the presence of the PDA layer. Furthermore, the elemental mapping images of HNTs@PDA shows that the Al, Si, and O elements are distributed throughout the HNTs, while the C and N elements of the PDA structure cover the whole HNTs and are uniformly distributed (Figure 4e). These visual results also further confirm the successful in situ generation of PDA on the surface of HNTs.

Figure 4 TEM and mapping images of functional nanofillers: (a) and (b) HNTs; (c) and (d) HNTs@PDA; (e) the elemental mapping images of HNTs@PDA.
Figure 4

TEM and mapping images of functional nanofillers: (a) and (b) HNTs; (c) and (d) HNTs@PDA; (e) the elemental mapping images of HNTs@PDA.

3.2 Structure and properties of nanocomposites

The morphologies of PEN- and CPEN-based nanocomposite film were characterized by SEM, respectively. It can be observed from Figure 5(a) that the pure PEN films have smooth cross-sections. Figure 5(b) shows the morphology of PEN/HNTs 20, it is clear that most of HNTs are exposed on the surface of the PEN matrix, and obvious separation and agglomeration between HNTs and PEN matrix is observed. This is due to the weak interface interaction between HNTs and PEN, which leads to local agglomeration in the PEN matrix. On the contrary, after PDA modification, the HNTs@PDA hybrids are more uniformly distributed in PEN without obvious aggregation, and the HNTs@PDA are all wrapped by the PEN matrix with no obvious HNTs alone in the cross-section (Figure 5(c)). It is mainly attributed to the reduction in the agglomeration of HNTs covered by dopamine self-polymerization [27]. At the same time, as the PDA molecule contains a benzene ring structure similar to that of PEN, the compatibility between them is improved. In addition, the abundant catechol groups on the PDA can react and adhere to the organic polymer, greatly improving the compatibility of the filler with the matrix. Therefore, it can be concluded that PDA-modified HNTs have better dispersion capacity in the PEN matrix [28].

Figure 5 The cross-section SEM images of composite films: (a) PEN; (b) PEN/HNTs 20; (c) PEN/HNTs@PDA 20; (a1) CPEN; (b1) CPEN/HNTs 20; (c1) CPEN/HNTs@PDA 20.
Figure 5

The cross-section SEM images of composite films: (a) PEN; (b) PEN/HNTs 20; (c) PEN/HNTs@PDA 20; (a1) CPEN; (b1) CPEN/HNTs 20; (c1) CPEN/HNTs@PDA 20.

In addition, the nanocomposites after high-temperature heat treatment were also investigated by SEM. The cross-section of all CPEN composite films shows a brittle break, and its surface is much flatter and smoother (Figure 5(a1–c1)), which is due to the fact that the –CN group on the PEN chain is cross-linked at high temperatures, generating a stable triazine ring. After the introduction of HNTs@PDA hybrids, the composite film exhibits excellent interfacial compatibility due to the triazine ring structure formed by the nitrile groups between the PEN molecular chains, which enhances the interfacial interaction and further improves the compatibility of the HNTs@PDA with the PEN matrix, thereby further reducing the agglomeration of HNTs@PDA hybrids.

To investigate the microstructure of HNTs in the PEN matrix before and after modification, the XRD of the PEN nanocomposites with different filler contents were tested separately, which are shown in Figure 6a. It can be seen from the Figure that all composite films have obvious diffraction peaks at 2θ = 12.2°, 20°, and 24.6°, which are attributed to the (001), (110), and (002) crystal planes of HNTs, respectively [21]. In addition, the XRD tests were also performed on the composite films after heat treatment. As shown in Figure 6b, the structure of CPEN/HNTs@PDA composite films shows a similar phenomenon to that of PEN/HNTs@PDA, and the results show that the crystal structure of the HNTs@PDA remains intact after high-temperature heat treatment, which provides a theoretical basis for the application in high-temperature environments.

Figure 6 XRD patterns of nanocomposite films: (a) PEN/HNTs@PDA; (b) CPEN/HNTs@PDA.
Figure 6

XRD patterns of nanocomposite films: (a) PEN/HNTs@PDA; (b) CPEN/HNTs@PDA.

The mechanical properties of composite materials are an important index parameter in industrial applications, which affect the value of materials in practical applications. The mechanical properties of PEN/HNTs@PDA films are shown in Figure 7. The results show that the tensile strength and modulus of pure PEN is 77.3 and 1957.2 MPa, respectively. However, the incorporation of HNTs@PDA fillers significantly alters the mechanical properties of the PEN composite film, exhibiting an overall trend of initial improvement followed by a decrease. After adding 5 wt% HNTs@PDA filler, the tensile strength and modulus increase to 83.3 and 2300.3 MPa, respectively. After the filler mass fraction exceeded 10 wt%, the tensile strength and modulus of the nanocomposites begin to gradually decrease. The above results are mainly due to the fact that the HNTs@PDA is an inorganic nanotube material with a relatively large length and diameter. When a certain concentration is reached, it can entangle with the PEN molecular chain, forming a physical cross-linking network in the composite system, which can enhance the physical and mechanical meshing between the HNTs@PDA and PEN matrix, thereby hindering the movement of the polymer molecular chain. When the material is subjected to external forces, it is transferred to rigid nanotubes, which will enhance the strength and modulus of the nanocomposites [29]. However, when the amount of HNTs@PDA filler is added to a certain extent, agglomeration between the HNTs@PDA may inevitably occur, resulting in a decrease in tensile strength and modulus. In addition, the elongation at break of the PEN/HNTs@PDA nanocomposites showed a tendency to increase and then decrease with the increase in the filler content, reaching a maximum value of 5.9%. This is mainly due to the fact that a small amount of HNTs@PDA has good compatibility with PEN and increases the plasticity of the nanocomposites due to the presence of PDA, which increases the elongation at break of the nanocomposites. However, with the further increase in HNTs@PDA content, the agglomeration between the HNTs@PDA may inevitably occur, which leads to a significant decrease in tensile strength, resulting in a rapid decrease in elongation at break. These results indicate that filling with appropriate number of HNTs@PDA fillers can enhance the mechanical properties of nanocomposites.

Figure 7 Mechanical properties of PEN/HNTs@PDA composite films: (a) stress–strain curves; (b) tensile strength; (c) tensile modulus; and (d) elongation at break.
Figure 7

Mechanical properties of PEN/HNTs@PDA composite films: (a) stress–strain curves; (b) tensile strength; (c) tensile modulus; and (d) elongation at break.

To further validate the impact of the modified filler on the mechanical properties of nanocomposites, the mechanical properties of PEN/HNTs and PEN/HNTs@PDA were analyzed and are presented in Figure 8. By comparing with PEN/HNTs, the mechanical properties of PEN/HNTs@PDA composite films are significantly improved. This is mainly due to the following reasons: (1) the introduction of PDA makes HNTs@PDA hybrids have high repulsion and relatively small specific surface energy, which can be well dispersed in the polymer matrix, resulting in difficulty to agglomerate, and avoids pores and defects in the composite film; (2) the existence of PDA greatly improves the interface compatibility between the HNTs@PDA and the PEN matrix, which further avoids the mechanical defects in the composite film; (3) the hydroxyl groups on the surface of PDA can form hydrogen bonds with the nitrile groups in the PEN molecular chain, thereby increasing the interaction of nanocomposites, and the corresponding mechanism diagram is shown in Figure 9. In summary, modification of HNTs with PDA can effectively enhance the mechanical properties of the PEN nanocomposites.

Figure 8 Mechanical properties of PEN composite films: (a) stress–strain curves; (b) tensile strength; (c) tensile modulus; and (d) elongation at break.
Figure 8

Mechanical properties of PEN composite films: (a) stress–strain curves; (b) tensile strength; (c) tensile modulus; and (d) elongation at break.

Figure 9 Schematic diagram of the internal structure before and after heat treatment of PEN nanocomposite film.
Figure 9

Schematic diagram of the internal structure before and after heat treatment of PEN nanocomposite film.

In addition, when pure PEN is subjected to high temperature heat treatment, its tensile modulus is further improved, and the corresponding stress–strain curve is shown in Figure S3. This enhancement can primarily be attributed to the chemical reaction of the nitrile groups within the PEN molecular chain at elevated temperatures, leading to the formation of triazine rings and the establishment of a chemical cross-linking network. Figure 9 shows the schematic diagram of the corresponding mechanism, and the FTIR spectrum of PEN before and after the reaction is shown in Figure S4. It is clear that the peak of 2,240 cm−1 belongs to the characteristic stretching band of the nitrile group. After heat treatment, it can be clearly seen from the CPEN curve that absorption peaks appear at 1,520 and 1,360 cm−1, which are mainly specific absorption bands of triazine rings [30,31]. The results further confirm the production of triazine rings in CPEN films, resulting in the formation of a chemical cross-linking network inside its molecules.

In addition, the physical images of PEN composite films are shown in Figure S5. The PEN/HNTs@PDA composite film can be arbitrarily rolled into different shapes, even when the filler content is as high as 20%. In addition, even after the composite film is heat treated, CPEN/HNTs@PDA still retains excellent flexibility. Therefore, the abovementioned PEN nanocomposites have potential application prospects as the flexible electronic devices.

Figure 10(a) shows the effect of the variation in the mass fraction of functionalized HNTs filler on the glass transition temperature (T g) of the PEN nanocomposites. The T g of the pure PEN is 150.5°C, and the thermal stability gradually increases with the increase in the mass fraction of HNTs@PDA from 154.4 to 167.8°C. This is because the HNTs@PDA filler is entangled with the PEN molecular chain in matrix resin and played a role in limiting the PEN molecular chain movement. In addition, the modification of filler facilitates the formation of a heat-resistant interface between the filler and the polymer matrix [32]. Herein, with the increase in the mass fraction of filler, the movement of polymer molecular chains is further restricted. Furthermore, the formation of hydroxyl groups on the PDA and nitrile groups on the PEN molecular chains makes the glass transition temperature to increase [33,34].

Figure 10 The DSC curves of composite films: (a) PEN/HNTs@PDA and (b) CPEN/HNTs@PDA.
Figure 10

The DSC curves of composite films: (a) PEN/HNTs@PDA and (b) CPEN/HNTs@PDA.

Meanwhile, the T g of CPEN/HNTs@PDA composite dielectric films was characterized by DSC. As shown in Figure 10(b), the T g of CPEN nanocomposites increased after high-temperature heat treatment, and T g of CPEN/HNTs@PDA increased from 167.8 to 215.5°C. This result is due to the formation of triazine rings by the nitrile group between the PEN molecular chains, which further impede the movement of the molecular chains, resulting in a further increase in the T g of the composite film [35,36], the corresponding internal mechanism diagram is shown in Figure 9.

To further investigate the degree of cross-linking of PEN nanocomposite films, in this work, the gel content of the nanocomposites was measured by Soxhlet extraction. The corresponding experimental methods and calculation formulas (equation S1) are listed in the supplementary information. As shown in Figure 11, the gel content of all nanocomposites is greater than 90%, which indicates that these films have a very high degree of cross-linking. This is due to the thermally induced self-cross-linking reaction of nitrile group on the PEN chain to form a triazine ring, producing cross-linked CPEN. This finding is consistent with the results obtained from the DSC tests [30,31].

Figure 11 Gel content of CPEN/HNTs@PDA composite films.
Figure 11

Gel content of CPEN/HNTs@PDA composite films.

Figure 12(a1–e1) shows the center-temperature of the PEN composite films filled with different HNTs@PDA contents after 10 s of laser irradiation. As the filler increases, the thermal conductivity of the composite films becomes more pronounced and the central temperature of the films gradually increases up to 49.7°C for PEN/HNTs@PDA 20. This is due to the gradual introduction of the HNTs ceramic filler, which promotes the thermal conductivity of the composite. Meanwhile, Figure 12(a2–e2) shows the center-temperature of the CPEN composite films after 10 s of laser irradiation. The center-temperature of all CPEN nanocomposites is higher than that of PEN nanocomposites, which is due to the formation of a triazine ring by the nitrile group between PEN molecular chains and the formation of hydrogen bonds between the hydroxyl groups on the PDA and the nitrile groups on the PEN molecular chains, which enhances the interfacial forces and promotes the further improvement of the thermal conductivity of the nanocomposites [37].

Figure 12 Infrared thermographic image of composite film with different HNTs@PDA hybrids: (a1) PEN; (a2) CPEN; (b1 and b2) 5 wt%; (c1 and c2) 10 wt%; (d1 and d2) 15 wt%; (e1 and e2) 20 wt%; (f1 and f2) the center-temperature of nanocomposites;.
Figure 12

Infrared thermographic image of composite film with different HNTs@PDA hybrids: (a1) PEN; (a2) CPEN; (b1 and b2) 5 wt%; (c1 and c2) 10 wt%; (d1 and d2) 15 wt%; (e1 and e2) 20 wt%; (f1 and f2) the center-temperature of nanocomposites;.

Figure 13(a) shows the dielectric constant of the PEN/HNTs@PDA nanocomposites at room temperature, from which it can be observed that the change in dielectric constant with frequency is relatively stable for pure PEN film. It exhibits good dielectric properties-frequency stability. when the filler content is greater than 10 wt%, the dielectric constant of nanocomposites appears to be significantly improved. As can be found in Figure 13(a) and Figure S6(a), compared with the pure PEN film (3.6 at 1 kHz), the dielectric constants of the nanocomposites are 8.6 and 11.6 (1 kHz) when the HNTs@PDA content is 15 and 20 wt%, respectively, which are 2.4 and 3.2 times larger than pure PEN. And the change in dielectric constant with frequency gradually increases, the dielectric constant-frequency stability gradually decreases. This is due to the large specific surface area of HNTs, which is conducive to the formation of micro-capacitance inside the PEN matrix and the formation of Maxwell–Wagner–Sillars polarization with high intensity with the applied electric field [38,39]. Therefore, the dielectric constants of the nanocomposites are greatly enhanced. In addition, the dielectric constant gradually decreases with the increase in the test frequency, which is because the polarization speed in the system cannot keep up with the electric field frequency change, resulting in the polarization hysteresis phenomenon [40,41,42].

Figure 13 Dielectric properties of nanocomposite films: (a) and (b) PEN/HNTs@PDA and (c) and (d) CPEN/HNTs@PDA.
Figure 13

Dielectric properties of nanocomposite films: (a) and (b) PEN/HNTs@PDA and (c) and (d) CPEN/HNTs@PDA.

Meanwhile, Figure 13(b) and Figure S6(b) show the dielectric loss–frequency curves of the PEN/HNTs@PDA nanocomposite films. With the rise of filler content, the dielectric loss of films gradually increases. However, the dielectric loss of several nanocomposites with different contents is less than 0.03, remaining at a relatively low level, which can be well applied to practical production [43]. As shown in Figure 13(c) and (d) and Figure S6(c) and (d), on comparing with the PEN/HNTs@PDA composite films, the dielectric properties-frequency of CPEN/HNTs@PDA are more stable, which is mainly attributed to the formation of cross-linking network, which hinders the movement of molecular chains and reduces the internal polarization of molecules. In addition, the hydrogen bond formed between the HNTs@PDA and the PEN matrix reduces the interfacial polarization of the system. Therefore, the dielectric performance-frequency relationship of CPEN composite film is more stable.

Figure 14 shows the dielectric performance–temperature relationship curves of the composite films, from which it can be seen that when the temperature is below the T g of the nanocomposites, their dielectric constant remains stable. However, when the temperature exceeds the T g, the dielectric constant increases sharply. Usually, when the test temperature exceeds the T g of the composite film, the polymer molecular chain begins to move violently, and the movement of the free charge inside the molecule intensifies. Therefore, the polarization effect inside the composite film increases, and the macroscopic manifestation is a sharp increase in the dielectric constant [44,45]. Another phenomenon is that the dielectric constant-temperature stability of CPEN/HNTs@PDA nanocomposites is significantly better than that of PEN/HNTs@PDA (Figure 14(a) and (c)). This is mainly because after heat treatment, a triazine ring is generated inside the CPEN/HNTs@PDA composite films, forming a large number of cross-linked networks, thereby obtaining higher T g. Therefore, the CPEN composite films have better dielectric properties-temperature stability [30,46].

Figure 14 Dielectric properties of composite films: (a) and (c) temperature-permittivity relationship diagram and (b) and (d) dielectric constant-temperature coefficient.
Figure 14

Dielectric properties of composite films: (a) and (c) temperature-permittivity relationship diagram and (b) and (d) dielectric constant-temperature coefficient.

In addition, the dielectric constant-temperature coefficient is calculated by equation S2 [46]. The final calculated results are shown in Figure 14(b) and (d). It is clear that when the test temperature is from 25 to 160°C, the dielectric constant-temperature coefficient of the nanocomposite film is lower than 2 × 10−3°C−1, indicating that the composite film has good dielectric constant-temperature coefficient stability in this temperature range. However, when the temperature exceeds 160°C, the dielectric constant-temperature coefficient increases significantly. Comparing the results of PEN/HNTs@PDA with CPEN/HNTs@PDA, it is observed that the dielectric constant-temperature coefficient of CPEN/HNTs@PDA composite films remains consistently low within the temperature range of 25–180°C, all being less than 7 × 10−4°C⁻¹ (Figure 14(c) and (d) and Figure S7). This is because the cross-linking network inside the CPEN composite film greatly restricts the movement of the CPEN molecular segment, so all CPEN composite films have better temperature coefficient and dielectric constant. This result confirms that the CPEN composite film has excellent dielectric stability at high temperature, which means that it can be used in practical applications at 180°C.

Moreover, to further clearly demonstrate the performance of CPEN/HNTs@PDA nanocomposites, the dielectric properties and working temperature of different nanocomposites containing HNTs at room temperature are summarized in Table 1. Among them, most nanocomposites have a dielectric constant lower than 5, and the working temperature of PLA/HNTs, PEDOT/PVDF-HNTs, and Epoxy/m-HNTs is less than 160°C. In comparison, the CPEN/HNTs@PDA nanocomposites in this work has a high dielectric constant and a very low dielectric loss, and it can be used as dielectric films in environments with the working temperatures up to 180°C.

Table 1

Comparison of dielectric properties of different composite dielectric materials

Samples Content (%) Dielectric constant (1 kHz) Dielectric loss (1 kHz) Working temperature (°C) Ref.
PLA/HNTs 10 0.26 ∼1.480 62.2 [47]
PEDOT/PVDF-HNTs 7 ∼75 ∼0.150 160.0 [48]
IPTS/SiR-HNTs 9 ∼6.2 ∼0.070 — [49]
P(VDF-CTFE)/HNTs 5 ∼18 ∼0.054 — [11]
PC/HNTs 6 ∼3.7 0.118 — [50]
PVB/HNTs 10 ∼3.8 ∼0.030 — [51]
PI/HNTs 10 ∼3.8 ∼0.010 — [52]
PEN/HNTs@PDA 10 6.26 0.022 ∼160 This work
CPEN/HNTs@PDA 10 6.10 0.021 ∼180 This work

Figure 15 shows the water absorption rate of composite films with different filler contents, and the corresponding calculation formula (equation S3) is listed in the supplementary information. The results show that the water absorption rate of all nanocomposites is less than 0.9%. Owing to the nitrile group in the PEN molecular chain, the PEN composite film has good hydrophobicity. After high temperature heat treatment, the PEN molecular chains are cross-linked with each other to form a cross-linking network, resulting in lower water absorption of CPEN composite films [35]. This result provides a theoretical basis for the application of this kind of composite film in various electronic and electrical fields [36,53,54].

Figure 15 Water absorption of composite films.
Figure 15

Water absorption of composite films.

4 Conclusion

In conclusion, this work develops a straightforward method to prepare PEN nanocomposites. The HNTs were coated by PDA through in situ polymerization to form a core-shell structure HNTs@PDA, which were then introduced into the PEN matrix as functional fillers. The hydrogen bond formed between the nitrile group and hydroxyl group improves the interface interaction between the HNTs@PDA and the PEN matrix, which makes the PEN/HNTs@PDA nanocomposites have good interfacial compatibility, and mechanical and dielectric properties. When the filler content is 5 wt%, the tensile strength and modulus of the composite film reach 83.3 and 2300.3 MPa, respectively, which is much higher than that of PEN. Besides, dielectric constant of PEN/HNTs@PDA 20 is 11.56 at 1 kHz. In addition, after high-temperature heat treatment, a chemical cross-linking reaction occurred within the PEN matrix, further enhancing the thermal stability of the nanocomposite films. The results show that the T g of CPEN/HNTs@PDA 20 composite film reaches 215.5°C, which is 47.7°C higher than that of PEN/HNTs@PDA 20. Furthermore, the dielectric constant-temperature coefficient of all CPEN composite films is less than 7 × 10−4°C−1 at the temperature range of 25–180°C. Overall, this work provides a simple and environmentally friendly approach for the fabrication of high-performance composite dielectric films suitable for organic film capacitors.

# These authors contributed equally to this work and should be considered first co-authors.

  1. Funding information: This work was supported by National Natural Science Foundation of China (No. 52203102), the Natural Science Foundation of Sichuan Province (2022NSFSC2009), the Fundamental Research Funds for the Central Universities, Southwest Minzu University (ZYN2023096), and the Science and Technology Planning Project of Longquanyi, Chengdu (No. LQXKJ-KJXM-2022-04).

  2. Author contributions: All authors have accepted responsibility for the entire content of this manuscript and approved its submission.

  3. Conflict of interest: The authors state no conflict of interest.

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Received: 2023-06-04
Revised: 2023-07-21
Accepted: 2023-08-12
Published Online: 2023-09-08

© 2023 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  39. Role of localized magnetic field in vortex generation in tri-hybrid nanofluid flow: A numerical approach
  40. Intelligent computing for the double-diffusive peristaltic rheology of magneto couple stress nanomaterials
  41. Bioconvection transport of upper convected Maxwell nanoliquid with gyrotactic microorganism, nonlinear thermal radiation, and chemical reaction
  42. 3D printing of porous Ti6Al4V bone tissue engineering scaffold and surface anodization preparation of nanotubes to enhance its biological property
  43. Bioinspired ferromagnetic CoFe2O4 nanoparticles: Potential pharmaceutical and medical applications
  44. Significance of gyrotactic microorganisms on the MHD tangent hyperbolic nanofluid flow across an elastic slender surface: Numerical analysis
  45. Performance of polycarboxylate superplasticisers in seawater-blended cement: Effect from chemical structure and nano modification
  46. Entropy minimization of GO–Ag/KO cross-hybrid nanofluid over a convectively heated surface
  47. Oxygen plasma assisted room temperature bonding for manufacturing SU-8 polymer micro/nanoscale nozzle
  48. Performance and mechanism of CO2 reduction by DBD-coupled mesoporous SiO2
  49. Polyarylene ether nitrile dielectric films modified by HNTs@PDA hybrids for high-temperature resistant organic electronics field
  50. Exploration of generalized two-phase free convection magnetohydrodynamic flow of dusty tetra-hybrid Casson nanofluid between parallel microplates
  51. Hygrothermal bending analysis of sandwich nanoplates with FG porous core and piezomagnetic faces via nonlocal strain gradient theory
  52. Design and optimization of a TiO2/RGO-supported epoxy multilayer microwave absorber by the modified local best particle swarm optimization algorithm
  53. Mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2
  54. Self-template synthesis of hollow flower-like NiCo2O4 nanoparticles as an efficient bifunctional catalyst for oxygen reduction and oxygen evolution in alkaline media
  55. High-performance wearable flexible strain sensors based on an AgNWs/rGO/TPU electrospun nanofiber film for monitoring human activities
  56. High-performance lithium–selenium batteries enabled by nitrogen-doped porous carbon from peanut meal
  57. Investigating effects of Lorentz forces and convective heating on ternary hybrid nanofluid flow over a curved surface using homotopy analysis method
  58. Exploring the potential of biogenic magnesium oxide nanoparticles for cytotoxicity: In vitro and in silico studies on HCT116 and HT29 cells and DPPH radical scavenging
  59. Enhanced visible-light-driven photocatalytic degradation of azo dyes by heteroatom-doped nickel tungstate nanoparticles
  60. A facile method to synthesize nZVI-doped polypyrrole-based carbon nanotube for Ag(i) removal
  61. Improved osseointegration of dental titanium implants by TiO2 nanotube arrays with self-assembled recombinant IGF-1 in type 2 diabetes mellitus rat model
  62. Functionalized SWCNTs@Ag–TiO2 nanocomposites induce ROS-mediated apoptosis and autophagy in liver cancer cells
  63. Triboelectric nanogenerator based on a water droplet spring with a concave spherical surface for harvesting wave energy and detecting pressure
  64. A mathematical approach for modeling the blood flow containing nanoparticles by employing the Buongiorno’s model
  65. Molecular dynamics study on dynamic interlayer friction of graphene and its strain effect
  66. Induction of apoptosis and autophagy via regulation of AKT and JNK mitogen-activated protein kinase pathways in breast cancer cell lines exposed to gold nanoparticles loaded with TNF-α and combined with doxorubicin
  67. Effect of PVA fibers on durability of nano-SiO2-reinforced cement-based composites subjected to wet-thermal and chloride salt-coupled environment
  68. Effect of polyvinyl alcohol fibers on mechanical properties of nano-SiO2-reinforced geopolymer composites under a complex environment
  69. In vitro studies of titanium dioxide nanoparticles modified with glutathione as a potential drug delivery system
  70. Comparative investigations of Ag/H2O nanofluid and Ag-CuO/H2O hybrid nanofluid with Darcy-Forchheimer flow over a curved surface
  71. Study on deformation characteristics of multi-pass continuous drawing of micro copper wire based on crystal plasticity finite element method
  72. Properties of ultra-high-performance self-compacting fiber-reinforced concrete modified with nanomaterials
  73. Prediction of lap shear strength of GNP and TiO2/epoxy nanocomposite adhesives
  74. A novel exploration of how localized magnetic field affects vortex generation of trihybrid nanofluids
  75. Fabrication and physicochemical characterization of copper oxide–pyrrhotite nanocomposites for the cytotoxic effects on HepG2 cells and the mechanism
  76. Thermal radiative flow of cross nanofluid due to a stretched cylinder containing microorganisms
  77. In vitro study of the biphasic calcium phosphate/chitosan hybrid biomaterial scaffold fabricated via solvent casting and evaporation technique for bone regeneration
  78. Insights into the thermal characteristics and dynamics of stagnant blood conveying titanium oxide, alumina, and silver nanoparticles subject to Lorentz force and internal heating over a curved surface
  79. Effects of nano-SiO2 additives on carbon fiber-reinforced fly ash–slag geopolymer composites performance: Workability, mechanical properties, and microstructure
  80. Energy bandgap and thermal characteristics of non-Darcian MHD rotating hybridity nanofluid thin film flow: Nanotechnology application
  81. Green synthesis and characterization of ginger-extract-based oxali-palladium nanoparticles for colorectal cancer: Downregulation of REG4 and apoptosis induction
  82. Abnormal evolution of resistivity and microstructure of annealed Ag nanoparticles/Ag–Mo films
  83. Preparation of water-based dextran-coated Fe3O4 magnetic fluid for magnetic hyperthermia
  84. Statistical investigations and morphological aspects of cross-rheological material suspended in transportation of alumina, silica, titanium, and ethylene glycol via the Galerkin algorithm
  85. Effect of CNT film interleaves on the flexural properties and strength after impact of CFRP composites
  86. Self-assembled nanoscale entities: Preparative process optimization, payload release, and enhanced bioavailability of thymoquinone natural product
  87. Structure–mechanical property relationships of 3D-printed porous polydimethylsiloxane films
  88. Nonlinear thermal radiation and the slip effect on a 3D bioconvection flow of the Casson nanofluid in a rotating frame via a homotopy analysis mechanism
  89. Residual mechanical properties of concrete incorporated with nano supplementary cementitious materials exposed to elevated temperature
  90. Time-independent three-dimensional flow of a water-based hybrid nanofluid past a Riga plate with slips and convective conditions: A homotopic solution
  91. Lightweight and high-strength polyarylene ether nitrile-based composites for efficient electromagnetic interference shielding
  92. Review Articles
  93. Recycling waste sources into nanocomposites of graphene materials: Overview from an energy-focused perspective
  94. Hybrid nanofiller reinforcement in thermoset and biothermoset applications: A review
  95. Current state-of-the-art review of nanotechnology-based therapeutics for viral pandemics: Special attention to COVID-19
  96. Solid lipid nanoparticles for targeted natural and synthetic drugs delivery in high-incidence cancers, and other diseases: Roles of preparation methods, lipid composition, transitional stability, and release profiles in nanocarriers’ development
  97. Critical review on experimental and theoretical studies of elastic properties of wurtzite-structured ZnO nanowires
  98. Polyurea micro-/nano-capsule applications in construction industry: A review
  99. A comprehensive review and clinical guide to molecular and serological diagnostic tests and future development: In vitro diagnostic testing for COVID-19
  100. Recent advances in electrocatalytic oxidation of 5-hydroxymethylfurfural to 2,5-furandicarboxylic acid: Mechanism, catalyst, coupling system
  101. Research progress and prospect of silica-based polymer nanofluids in enhanced oil recovery
  102. Review of the pharmacokinetics of nanodrugs
  103. Engineered nanoflowers, nanotrees, nanostars, nanodendrites, and nanoleaves for biomedical applications
  104. Research progress of biopolymers combined with stem cells in the repair of intrauterine adhesions
  105. Progress in FEM modeling on mechanical and electromechanical properties of carbon nanotube cement-based composites
  106. Antifouling induced by surface wettability of poly(dimethyl siloxane) and its nanocomposites
  107. TiO2 aerogel composite high-efficiency photocatalysts for environmental treatment and hydrogen energy production
  108. Structural properties of alumina surfaces and their roles in the synthesis of environmentally persistent free radicals (EPFRs)
  109. Nanoparticles for the potential treatment of Alzheimer’s disease: A physiopathological approach
  110. Current status of synthesis and consolidation strategies for thermo-resistant nanoalloys and their general applications
  111. Recent research progress on the stimuli-responsive smart membrane: A review
  112. Dispersion of carbon nanotubes in aqueous cementitious materials: A review
  113. Applications of DNA tetrahedron nanostructure in cancer diagnosis and anticancer drugs delivery
  114. Magnetic nanoparticles in 3D-printed scaffolds for biomedical applications
  115. An overview of the synthesis of silicon carbide–boron carbide composite powders
  116. Organolead halide perovskites: Synthetic routes, structural features, and their potential in the development of photovoltaic
  117. Recent advancements in nanotechnology application on wood and bamboo materials: A review
  118. Application of aptamer-functionalized nanomaterials in molecular imaging of tumors
  119. Recent progress on corrosion mechanisms of graphene-reinforced metal matrix composites
  120. Research progress on preparation, modification, and application of phenolic aerogel
  121. Application of nanomaterials in early diagnosis of cancer
  122. Plant mediated-green synthesis of zinc oxide nanoparticles: An insight into biomedical applications
  123. Recent developments in terahertz quantum cascade lasers for practical applications
  124. Recent progress in dielectric/metal/dielectric electrodes for foldable light-emitting devices
  125. Nanocoatings for ballistic applications: A review
  126. A mini-review on MoS2 membrane for water desalination: Recent development and challenges
  127. Recent updates in nanotechnological advances for wound healing: A narrative review
  128. Recent advances in DNA nanomaterials for cancer diagnosis and treatment
  129. Electrochemical micro- and nanobiosensors for in vivo reactive oxygen/nitrogen species measurement in the brain
  130. Advances in organic–inorganic nanocomposites for cancer imaging and therapy
  131. Advancements in aluminum matrix composites reinforced with carbides and graphene: A comprehensive review
  132. Modification effects of nanosilica on asphalt binders: A review
  133. Decellularized extracellular matrix as a promising biomaterial for musculoskeletal tissue regeneration
  134. Review of the sol–gel method in preparing nano TiO2 for advanced oxidation process
  135. Micro/nano manufacturing aircraft surface with anti-icing and deicing performances: An overview
  136. Cell type-targeting nanoparticles in treating central nervous system diseases: Challenges and hopes
  137. An overview of hydrogen production from Al-based materials
  138. A review of application, modification, and prospect of melamine foam
  139. A review of the performance of fibre-reinforced composite laminates with carbon nanotubes
  140. Research on AFM tip-related nanofabrication of two-dimensional materials
  141. Advances in phase change building materials: An overview
  142. Development of graphene and graphene quantum dots toward biomedical engineering applications: A review
  143. Nanoremediation approaches for the mitigation of heavy metal contamination in vegetables: An overview
  144. Photodynamic therapy empowered by nanotechnology for oral and dental science: Progress and perspectives
  145. Biosynthesis of metal nanoparticles: Bioreduction and biomineralization
  146. Current diagnostic and therapeutic approaches for severe acute respiratory syndrome coronavirus-2 (SARS-COV-2) and the role of nanomaterial-based theragnosis in combating the pandemic
  147. Application of two-dimensional black phosphorus material in wound healing
  148. Special Issue on Advanced Nanomaterials and Composites for Energy Conversion and Storage - Part I
  149. Helical fluorinated carbon nanotubes/iron(iii) fluoride hybrid with multilevel transportation channels and rich active sites for lithium/fluorinated carbon primary battery
  150. The progress of cathode materials in aqueous zinc-ion batteries
  151. Special Issue on Advanced Nanomaterials for Carbon Capture, Environment and Utilization for Energy Sustainability - Part I
  152. Effect of polypropylene fiber and nano-silica on the compressive strength and frost resistance of recycled brick aggregate concrete
  153. Mechanochemical design of nanomaterials for catalytic applications with a benign-by-design focus
https://doi.org/10.1515/ntrev-2023-0117
Schlagwörter für diesen Artikel
polyarylene ether nitrile; nanocomposites; dielectric properties; core-shell structure
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Research Articles
  2. Preparation of CdS–Ag2S nanocomposites by ultrasound-assisted UV photolysis treatment and its visible light photocatalysis activity
  3. Significance of nanoparticle radius and inter-particle spacing toward the radiative water-based alumina nanofluid flow over a rotating disk
  4. Aptamer-based detection of serotonin based on the rapid in situ synthesis of colorimetric gold nanoparticles
  5. Investigation of the nucleation and growth behavior of Ti2AlC and Ti3AlC nano-precipitates in TiAl alloys
  6. Dynamic recrystallization behavior and nucleation mechanism of dual-scale SiCp/A356 composites processed by P/M method
  7. High mechanical performance of 3-aminopropyl triethoxy silane/epoxy cured in a sandwich construction of 3D carbon felts foam and woven basalt fibers
  8. Applying solution of spray polyurea elastomer in asphalt binder: Feasibility analysis and DSR study based on the MSCR and LAS tests
  9. Study on the chronic toxicity and carcinogenicity of iron-based bioabsorbable stents
  10. Influence of microalloying with B on the microstructure and properties of brazed joints with Ag–Cu–Zn–Sn filler metal
  11. Thermohydraulic performance of thermal system integrated with twisted turbulator inserts using ternary hybrid nanofluids
  12. Study of mechanical properties of epoxy/graphene and epoxy/halloysite nanocomposites
  13. Effects of CaO addition on the CuW composite containing micro- and nano-sized tungsten particles synthesized via aluminothermic coupling with silicothermic reduction
  14. Cu and Al2O3-based hybrid nanofluid flow through a porous cavity
  15. Design of functional vancomycin-embedded bio-derived extracellular matrix hydrogels for repairing infectious bone defects
  16. Study on nanocrystalline coating prepared by electro-spraying 316L metal wire and its corrosion performance
  17. Axial compression performance of CFST columns reinforced by ultra-high-performance nano-concrete under long-term loading
  18. Tungsten trioxide nanocomposite for conventional soliton and noise-like pulse generation in anomalous dispersion laser cavity
  19. Microstructure and electrical contact behavior of the nano-yttria-modified Cu-Al2O3/30Mo/3SiC composite
  20. Melting rheology in thermally stratified graphene-mineral oil reservoir (third-grade nanofluid) with slip condition
  21. Re-examination of nonlinear vibration and nonlinear bending of porous sandwich cylindrical panels reinforced by graphene platelets
  22. Parametric simulation of hybrid nanofluid flow consisting of cobalt ferrite nanoparticles with second-order slip and variable viscosity over an extending surface
  23. Chitosan-capped silver nanoparticles with potent and selective intrinsic activity against the breast cancer cells
  24. Multi-core/shell SiO2@Al2O3 nanostructures deposited on Ti3AlC2 to enhance high-temperature stability and microwave absorption properties
  25. Solution-processed Bi2S3/BiVO4/TiO2 ternary heterojunction photoanode with enhanced photoelectrochemical performance
  26. Electroporation effect of ZnO nanoarrays under low voltage for water disinfection
  27. NIR-II window absorbing graphene oxide-coated gold nanorods and graphene quantum dot-coupled gold nanorods for photothermal cancer therapy
  28. Nonlinear three-dimensional stability characteristics of geometrically imperfect nanoshells under axial compression and surface residual stress
  29. Investigation of different nanoparticles properties on the thermal conductivity and viscosity of nanofluids by molecular dynamics simulation
  30. Optimized Cu2O-{100} facet for generation of different reactive oxidative species via peroxymonosulfate activation at specific pH values to efficient acetaminophen removal
  31. Brownian and thermal diffusivity impact due to the Maxwell nanofluid (graphene/engine oil) flow with motile microorganisms and Joule heating
  32. Appraising the dielectric properties and the effectiveness of electromagnetic shielding of graphene reinforced silicone rubber nanocomposite
  33. Synthesis of Ag and Cu nanoparticles by plasma discharge in inorganic salt solutions
  34. Low-cost and large-scale preparation of ultrafine TiO2@C hybrids for high-performance degradation of methyl orange and formaldehyde under visible light
  35. Utilization of waste glass with natural pozzolan in the production of self-glazed glass-ceramic materials
  36. Mechanical performance of date palm fiber-reinforced concrete modified with nano-activated carbon
  37. Melting point of dried gold nanoparticles prepared with ultrasonic spray pyrolysis and lyophilisation
  38. Graphene nanofibers: A modern approach towards tailored gypsum composites
  39. Role of localized magnetic field in vortex generation in tri-hybrid nanofluid flow: A numerical approach
  40. Intelligent computing for the double-diffusive peristaltic rheology of magneto couple stress nanomaterials
  41. Bioconvection transport of upper convected Maxwell nanoliquid with gyrotactic microorganism, nonlinear thermal radiation, and chemical reaction
  42. 3D printing of porous Ti6Al4V bone tissue engineering scaffold and surface anodization preparation of nanotubes to enhance its biological property
  43. Bioinspired ferromagnetic CoFe2O4 nanoparticles: Potential pharmaceutical and medical applications
  44. Significance of gyrotactic microorganisms on the MHD tangent hyperbolic nanofluid flow across an elastic slender surface: Numerical analysis
  45. Performance of polycarboxylate superplasticisers in seawater-blended cement: Effect from chemical structure and nano modification
  46. Entropy minimization of GO–Ag/KO cross-hybrid nanofluid over a convectively heated surface
  47. Oxygen plasma assisted room temperature bonding for manufacturing SU-8 polymer micro/nanoscale nozzle
  48. Performance and mechanism of CO2 reduction by DBD-coupled mesoporous SiO2
  49. Polyarylene ether nitrile dielectric films modified by HNTs@PDA hybrids for high-temperature resistant organic electronics field
  50. Exploration of generalized two-phase free convection magnetohydrodynamic flow of dusty tetra-hybrid Casson nanofluid between parallel microplates
  51. Hygrothermal bending analysis of sandwich nanoplates with FG porous core and piezomagnetic faces via nonlocal strain gradient theory
  52. Design and optimization of a TiO2/RGO-supported epoxy multilayer microwave absorber by the modified local best particle swarm optimization algorithm
  53. Mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2
  54. Self-template synthesis of hollow flower-like NiCo2O4 nanoparticles as an efficient bifunctional catalyst for oxygen reduction and oxygen evolution in alkaline media
  55. High-performance wearable flexible strain sensors based on an AgNWs/rGO/TPU electrospun nanofiber film for monitoring human activities
  56. High-performance lithium–selenium batteries enabled by nitrogen-doped porous carbon from peanut meal
  57. Investigating effects of Lorentz forces and convective heating on ternary hybrid nanofluid flow over a curved surface using homotopy analysis method
  58. Exploring the potential of biogenic magnesium oxide nanoparticles for cytotoxicity: In vitro and in silico studies on HCT116 and HT29 cells and DPPH radical scavenging
  59. Enhanced visible-light-driven photocatalytic degradation of azo dyes by heteroatom-doped nickel tungstate nanoparticles
  60. A facile method to synthesize nZVI-doped polypyrrole-based carbon nanotube for Ag(i) removal
  61. Improved osseointegration of dental titanium implants by TiO2 nanotube arrays with self-assembled recombinant IGF-1 in type 2 diabetes mellitus rat model
  62. Functionalized SWCNTs@Ag–TiO2 nanocomposites induce ROS-mediated apoptosis and autophagy in liver cancer cells
  63. Triboelectric nanogenerator based on a water droplet spring with a concave spherical surface for harvesting wave energy and detecting pressure
  64. A mathematical approach for modeling the blood flow containing nanoparticles by employing the Buongiorno’s model
  65. Molecular dynamics study on dynamic interlayer friction of graphene and its strain effect
  66. Induction of apoptosis and autophagy via regulation of AKT and JNK mitogen-activated protein kinase pathways in breast cancer cell lines exposed to gold nanoparticles loaded with TNF-α and combined with doxorubicin
  67. Effect of PVA fibers on durability of nano-SiO2-reinforced cement-based composites subjected to wet-thermal and chloride salt-coupled environment
  68. Effect of polyvinyl alcohol fibers on mechanical properties of nano-SiO2-reinforced geopolymer composites under a complex environment
  69. In vitro studies of titanium dioxide nanoparticles modified with glutathione as a potential drug delivery system
  70. Comparative investigations of Ag/H2O nanofluid and Ag-CuO/H2O hybrid nanofluid with Darcy-Forchheimer flow over a curved surface
  71. Study on deformation characteristics of multi-pass continuous drawing of micro copper wire based on crystal plasticity finite element method
  72. Properties of ultra-high-performance self-compacting fiber-reinforced concrete modified with nanomaterials
  73. Prediction of lap shear strength of GNP and TiO2/epoxy nanocomposite adhesives
  74. A novel exploration of how localized magnetic field affects vortex generation of trihybrid nanofluids
  75. Fabrication and physicochemical characterization of copper oxide–pyrrhotite nanocomposites for the cytotoxic effects on HepG2 cells and the mechanism
  76. Thermal radiative flow of cross nanofluid due to a stretched cylinder containing microorganisms
  77. In vitro study of the biphasic calcium phosphate/chitosan hybrid biomaterial scaffold fabricated via solvent casting and evaporation technique for bone regeneration
  78. Insights into the thermal characteristics and dynamics of stagnant blood conveying titanium oxide, alumina, and silver nanoparticles subject to Lorentz force and internal heating over a curved surface
  79. Effects of nano-SiO2 additives on carbon fiber-reinforced fly ash–slag geopolymer composites performance: Workability, mechanical properties, and microstructure
  80. Energy bandgap and thermal characteristics of non-Darcian MHD rotating hybridity nanofluid thin film flow: Nanotechnology application
  81. Green synthesis and characterization of ginger-extract-based oxali-palladium nanoparticles for colorectal cancer: Downregulation of REG4 and apoptosis induction
  82. Abnormal evolution of resistivity and microstructure of annealed Ag nanoparticles/Ag–Mo films
  83. Preparation of water-based dextran-coated Fe3O4 magnetic fluid for magnetic hyperthermia
  84. Statistical investigations and morphological aspects of cross-rheological material suspended in transportation of alumina, silica, titanium, and ethylene glycol via the Galerkin algorithm
  85. Effect of CNT film interleaves on the flexural properties and strength after impact of CFRP composites
  86. Self-assembled nanoscale entities: Preparative process optimization, payload release, and enhanced bioavailability of thymoquinone natural product
  87. Structure–mechanical property relationships of 3D-printed porous polydimethylsiloxane films
  88. Nonlinear thermal radiation and the slip effect on a 3D bioconvection flow of the Casson nanofluid in a rotating frame via a homotopy analysis mechanism
  89. Residual mechanical properties of concrete incorporated with nano supplementary cementitious materials exposed to elevated temperature
  90. Time-independent three-dimensional flow of a water-based hybrid nanofluid past a Riga plate with slips and convective conditions: A homotopic solution
  91. Lightweight and high-strength polyarylene ether nitrile-based composites for efficient electromagnetic interference shielding
  92. Review Articles
  93. Recycling waste sources into nanocomposites of graphene materials: Overview from an energy-focused perspective
  94. Hybrid nanofiller reinforcement in thermoset and biothermoset applications: A review
  95. Current state-of-the-art review of nanotechnology-based therapeutics for viral pandemics: Special attention to COVID-19
  96. Solid lipid nanoparticles for targeted natural and synthetic drugs delivery in high-incidence cancers, and other diseases: Roles of preparation methods, lipid composition, transitional stability, and release profiles in nanocarriers’ development
  97. Critical review on experimental and theoretical studies of elastic properties of wurtzite-structured ZnO nanowires
  98. Polyurea micro-/nano-capsule applications in construction industry: A review
  99. A comprehensive review and clinical guide to molecular and serological diagnostic tests and future development: In vitro diagnostic testing for COVID-19
  100. Recent advances in electrocatalytic oxidation of 5-hydroxymethylfurfural to 2,5-furandicarboxylic acid: Mechanism, catalyst, coupling system
  101. Research progress and prospect of silica-based polymer nanofluids in enhanced oil recovery
  102. Review of the pharmacokinetics of nanodrugs
  103. Engineered nanoflowers, nanotrees, nanostars, nanodendrites, and nanoleaves for biomedical applications
  104. Research progress of biopolymers combined with stem cells in the repair of intrauterine adhesions
  105. Progress in FEM modeling on mechanical and electromechanical properties of carbon nanotube cement-based composites
  106. Antifouling induced by surface wettability of poly(dimethyl siloxane) and its nanocomposites
  107. TiO2 aerogel composite high-efficiency photocatalysts for environmental treatment and hydrogen energy production
  108. Structural properties of alumina surfaces and their roles in the synthesis of environmentally persistent free radicals (EPFRs)
  109. Nanoparticles for the potential treatment of Alzheimer’s disease: A physiopathological approach
  110. Current status of synthesis and consolidation strategies for thermo-resistant nanoalloys and their general applications
  111. Recent research progress on the stimuli-responsive smart membrane: A review
  112. Dispersion of carbon nanotubes in aqueous cementitious materials: A review
  113. Applications of DNA tetrahedron nanostructure in cancer diagnosis and anticancer drugs delivery
  114. Magnetic nanoparticles in 3D-printed scaffolds for biomedical applications
  115. An overview of the synthesis of silicon carbide–boron carbide composite powders
  116. Organolead halide perovskites: Synthetic routes, structural features, and their potential in the development of photovoltaic
  117. Recent advancements in nanotechnology application on wood and bamboo materials: A review
  118. Application of aptamer-functionalized nanomaterials in molecular imaging of tumors
  119. Recent progress on corrosion mechanisms of graphene-reinforced metal matrix composites
  120. Research progress on preparation, modification, and application of phenolic aerogel
  121. Application of nanomaterials in early diagnosis of cancer
  122. Plant mediated-green synthesis of zinc oxide nanoparticles: An insight into biomedical applications
  123. Recent developments in terahertz quantum cascade lasers for practical applications
  124. Recent progress in dielectric/metal/dielectric electrodes for foldable light-emitting devices
  125. Nanocoatings for ballistic applications: A review
  126. A mini-review on MoS2 membrane for water desalination: Recent development and challenges
  127. Recent updates in nanotechnological advances for wound healing: A narrative review
  128. Recent advances in DNA nanomaterials for cancer diagnosis and treatment
  129. Electrochemical micro- and nanobiosensors for in vivo reactive oxygen/nitrogen species measurement in the brain
  130. Advances in organic–inorganic nanocomposites for cancer imaging and therapy
  131. Advancements in aluminum matrix composites reinforced with carbides and graphene: A comprehensive review
  132. Modification effects of nanosilica on asphalt binders: A review
  133. Decellularized extracellular matrix as a promising biomaterial for musculoskeletal tissue regeneration
  134. Review of the sol–gel method in preparing nano TiO2 for advanced oxidation process
  135. Micro/nano manufacturing aircraft surface with anti-icing and deicing performances: An overview
  136. Cell type-targeting nanoparticles in treating central nervous system diseases: Challenges and hopes
  137. An overview of hydrogen production from Al-based materials
  138. A review of application, modification, and prospect of melamine foam
  139. A review of the performance of fibre-reinforced composite laminates with carbon nanotubes
  140. Research on AFM tip-related nanofabrication of two-dimensional materials
  141. Advances in phase change building materials: An overview
  142. Development of graphene and graphene quantum dots toward biomedical engineering applications: A review
  143. Nanoremediation approaches for the mitigation of heavy metal contamination in vegetables: An overview
  144. Photodynamic therapy empowered by nanotechnology for oral and dental science: Progress and perspectives
  145. Biosynthesis of metal nanoparticles: Bioreduction and biomineralization
  146. Current diagnostic and therapeutic approaches for severe acute respiratory syndrome coronavirus-2 (SARS-COV-2) and the role of nanomaterial-based theragnosis in combating the pandemic
  147. Application of two-dimensional black phosphorus material in wound healing
  148. Special Issue on Advanced Nanomaterials and Composites for Energy Conversion and Storage - Part I
  149. Helical fluorinated carbon nanotubes/iron(iii) fluoride hybrid with multilevel transportation channels and rich active sites for lithium/fluorinated carbon primary battery
  150. The progress of cathode materials in aqueous zinc-ion batteries
  151. Special Issue on Advanced Nanomaterials for Carbon Capture, Environment and Utilization for Energy Sustainability - Part I
  152. Effect of polypropylene fiber and nano-silica on the compressive strength and frost resistance of recycled brick aggregate concrete
  153. Mechanochemical design of nanomaterials for catalytic applications with a benign-by-design focus
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Heruntergeladen am 12.9.2025 von https://www.degruyterbrill.com/document/doi/10.1515/ntrev-2023-0117/html
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