Startseite Naturwissenschaften Polyarylene ether nitrile and boron nitride composites: coating with sulfonated polyarylene ether nitrile
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Polyarylene ether nitrile and boron nitride composites: coating with sulfonated polyarylene ether nitrile

  • Renbo Wei EMAIL logo , Qian Xiao , Chenhao Zhan , Yong You , Xuefei Zhou und Xiaobo Liu EMAIL logo
Veröffentlicht/Copyright: 8. Mai 2019
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e-Polymers
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Abstract

Boron nitride (BN) coated with sulfonated poly-arylene ether nitrile (SPEN) (BN@SPEN) was used as additive to enhance the thermal conductivity of polyarylene ether nitrile. BN@SPEN was prepared by coating BN micro-platelets with SPEN through ultrasonic technology combined with the post-treatment bonding process. The prepared BN@SPEN was characterized by FTIR, TGA, SEM and TEM, which confirmed the successful coating of BN micro-platelets. The obtained BN@SPEN was introduced into the PEN matrix to prepare composite films by a solution casting method. The compatibility between BN and PEN matrix was studied by using SEM observation and rheology measurement. Furthermore, thermal conductivity of BN@SPEN/PEN films were carefully characterized. Thermal conductivity of BN@SPEN/PEN films was increased to 0.69 W/(m⋅K) at 20 wt% content of BN@SPEN, having 138% increment comparing with pure PEN.

Keywords: polyarylene ether nitrile; boron nitride; surface coating; sulfonated polyarylene ether nitrile

1 Introduction

Polyarylene ether nitrile represents a new polymeric material (1, 2, 3). In recent years, both the scientific community and the related commercial groups have aroused great interest in research of PEN, because of its remarkable performances, including prominent thermal and mechanical properties (2, 3, 4). The nitrile group bonding on the aromatic ring of PEN exhibits strong polarity which facilitates the adhesion between main-chain of macromolecule and other substances, and visibly increase the dielectric property. Moreover, the second generation of PEN terminated with phthalonitrile has a higher processing temperature and wide range of applications. The introduced phthalonitrile on the terminal point of polyarylene ether nitrile macromolecule main-chain can crosslink to build phthalocyanine rings with high thermal stability (5, 6, 7).

To fulfill the application in high temperature atmosphere, it not only requires the material with high temperature resistance, but also with excellent thermal conductivity 8. Although PEN can feed many demands including high temperature fields and outstanding mechanical domains owing to its unique structure and intrinsic high glass transition temperature (9,10), PEN is considered as a thermal insulator like other polymers with low thermal conductivity (11). The most promising and effective method of improvement of the thermal conductivity of PEN is the incorporation of additives with high thermal conductivity (11). A multitude of additives, such as carbon, metal oxides, metal nitrides, clay (12, 13, 14), and boron nitride (BN) (15, 16, 18) have been used as the additives to enhance the thermal conductivity of polymers.

Among those high thermally conductive fillers, boron nitride (BN) is mostly studied because of its high temperature stability, superior mechanical strength, a large thermal conductivity and insulating property, etc (19, 20, 21, 22, 23). BN is attractive not only in academic research but also with numerous applications because of structural analog and isoelectronic counterpart of graphite (24). In addition, BN has special structure that the strong covalent bonds of BN between boron and nitrogen atoms are formed alternately and BN is a fine electrical insulating two-dimensional material, which leads BN to be a good candidate for the preparation of thermal and electrical insulating composites (25, 26, 27). Nevertheless, there is still a challenge that BN and polymer matrix show good compatibility.

In this study, the BN was firstly coated with sulfonated polyarylene ether nitrile (SPEN) offering BN@SPEN, and then the BN@SPEN was introduced into polyarylene ether nitrile (PEN) matrix to obtain BN@SPEN/PEN composites. FTIR, TGA, SEM and TEM confirmed the preparation of BN@SPEN. The SEM and rheometer were used to study the compatibility between BN and PEN. Improved thermal conductivity of PEN was observed after the incorporation of the BN@SPEN. In addition, thermal, mechanical properties were also carefully investigated.

2 Experimental section

2.1 Materials

BN micro-platelets was received from J&K chemicals. N-methylpyrrolidone, toluene and acetone were obtained from KeLong chemicals. 4-Nitrophthalonitrile was purchased from Alpha chemicals. Sigma-Aldrich provided potassium 2,5-dihydroxybenzenesulfonate (PDBS) and 2,6-difluorobenzonitrile (DFBN). HCl and Phenolphthalin (PPL) were obtained from Haihong Chemicals. Potassium carbonate (K2CO3), hydroquinone (HQ) and biphenyl (BP) were used as received without other treatment.

2.2 Synthesis of PEN and SPEN

Synthesis of PEN terminated with phthalonitrile (Figure 1) by nucleophilic aromatic substitution polymerization method was accorded to the previous literature (28). Sulfonated polyarylene ether nitrile (SPEN, Figure 1) used in this work was synthesized according to the literature via nucleophilic aromatic substitution reaction between PPL, PDBS and DFBN (29).

Figure 1 Structure of PEN and SPEN.
Figure 1

Structure of PEN and SPEN.

2.3 Preparation of BN@SPEN

The BN@SPEN was obtained by ultrasonic method combined with the post-treatment bonding process. BN micro-platelets (1.0 g) was dispersed with 20 mL deionized water in a three neck round bottle flask. A highly dispersed white suspension was obtained with the help of violent ultrasonic treatment and mechanical stirrer for 2 h. Simultaneously, a certain mass (0.4 g) of SPEN was dissolved in 10 mL deionized water with mechanical stirring. Then, the SPEN solution was tenderly transferred into the BN suspension, and then stirred for another 3 h with ultra-sonication. After that, the mixture was further stirred with ultra-sonication at 70°C to evaporate the solvent mostly. The obtained particles were added into a mortar and were grinded into powder. Finally, the sulfonated polyarylene ether nitrile coated BN (BN@SPEN) were obtained after treating at 200°C for 4 h.

2.4 Preparation of BN@SPEN/PEN composites

The BN@SPEN/PEN composite film was fabricated by solution casting method. At first, BN@SPEN with weight mass was added in a three neck flask with 10 mL NMP solvent, forming a dispersion after simultaneously mechanical stirring and ultra-sonication for 2 h. Meanwhile, a certain mass of PEN was transferred into another 100 mL three neck flask and dissolved in NMP solvent. Then, the PEN solution stirring at 100°C for 30 min was mixed with the BN@SPEN dispersion. After cooling down to room temperature, the mixture was further stirred with ultra-sonication for 60 min. At last, above mentioned mixture putting on a glass plate was dried at the temperature of 90, 120, 140 and 160°C each for 1 h and 200°C for 2 h. When the temperature reached the room temperature, BN@SPEN/PEN films with different BN@SPEN loading were obtained. The BN@SPEN/PEN films were named as PEN, BN@SPEN/PEN4, BN@SPEN/PEN8, BN@SPEN/PEN12, BN@SPEN/PEN16 and BN@SPEN/PEN20 with BN@SPEN loading of 0, 4, 8, 12, 16 and 20 wt% respectively. Besides, BN/ PEN composite film with 8 wt% BN was also prepared for comparison.

2.5 Characterization

FTIR (200SXV, Nicolet) was employed to characterize chemical structure of samples. The pressed specimen mixed with KBr was tested. Morphologies of BN@SPEN and BN@SPEN were characterized by SEM (JEOL, JSM-5900LV) handling at 20 kV. DSC (Q100, TA) was measured from 100 to 320°C at a heat rate of 10°C/min. TGA (Q50, TA) was conducted from 100 to 800°C in nitrogen at a heat rate of 20°C/min. The mechanical measurements were taken on Electromechanical Universal Testing Machine (SANS CMT6104) under ISO-527-3 standard. Dynamic thermomechanical analysis (DMA, Q800, TA) was tested from 50 to 360°C at a heat rate of 5°C/min. Rheometer (AR-G2, TA) with parallel plates was employed for the rheological measurements. Samples (Φ25 mm × 1 mm) were tested at 320°C from 0.10 to 100 rad/ s.

3 Result and discussion

3.1 Preparation of BN@SPEN

FTIR was used to verify the coating of BN with SPEN. Figure 2a is FTIR spectra of BN and BN@SPEN. FTIR peak at 1387 cm-1 of comes from B-N stretching vibration, FTIR peak at 809 cm-1 is B-N-B (30, 31, 32, 33, 34), and FTIR peak at 3423 cm-1 is ascribed as O-H at the surface of BN. In comparison, the peak at 1016 cm-1 on the FTIR spectrum of BN@SPEN is consistent with C-O bond (35), the FTIR band at 1605 cm-1 is from benzene rings at SPEN (36), and a weak peak located at 2233 cm-1 is consistent with nitrile groups (-CN) on SPEN (37). Figure 2b shows the TGA curves of BN, BN@SPEN and SPEN. TGA results were measured from room temperature to 800°C, and the residual mass at 790°C on the TGA curves were used for the calculation of the BN content in BN@SPEN. The residual mass of BN, SPEN and BN@SPEN at 790°C is 100%, 51.6% and 86.7% respectively. Consequently, the BN content in BN@SPEN is calculated to be 72.6 wt%. SEM was also used to characterize the coating of BN micro-platelets with SPEN (Figures 3a and 3b). The SEM images show that the BN micro-platelets are coated by SPEN shell forming the BN@SPEN. TEM image of BN@SPEN indicates that BN is adhered together by SPEN (Figure 3c). All the evidence is sufficient to prove that the preparation of BN@SPEN is successful.

Figure 2 (a) FTIR spectra of the BN@SPEN and BN; (b) TGA curves of BN, BN@SPEN and SPEN.
Figure 2

(a) FTIR spectra of the BN@SPEN and BN; (b) TGA curves of BN, BN@SPEN and SPEN.

Figure 3 SEM images of (a) BN and (b) BN@SPEN; (c) TEM image of BN@SPEN.
Figure 3

SEM images of (a) BN and (b) BN@SPEN; (c) TEM image of BN@SPEN.

3.2 Morphology of BN@SPEN/PEN

The structure of PEN is shown in Figure 1. The BN was coated with SPEN (BN@SPEN) to improve the compatibility between BN and PEN. To explore the dispersability and compatibility of BN fillers with the PEN matrix, the micro-morphologies of BN@SPEN/PEN and BN/ PEN were investigated by SEM observation under the same weight percent of BN (8.0 wt%). As shown in Figures 4a and 4b, the BN is well dispersed in the PEN matrix in BN@SPEN/PEN due to the SPEN shell on BN@SPEN. In addition, a ductile section with ridge pattern is observed of the cross-section of BN@SPEN/PEN. When 20 wt% of BN@SPEN was incorporated, the BN is still well dispersed in the matrix

Figure 4 (a) and (b) Cross-sectional SEM images of the BN@SPEN/PEN composite with 8 wt% of BN@SPEN; (c) and (d) SEM images of the BN@SPEN/PEN composite with 20 wt% of BN; (e)-(f) SEM images of the BN/PEN composite film with 8 wt% of BN.
Figure 4

(a) and (b) Cross-sectional SEM images of the BN@SPEN/PEN composite with 8 wt% of BN@SPEN; (c) and (d) SEM images of the BN@SPEN/PEN composite with 20 wt% of BN; (e)-(f) SEM images of the BN/PEN composite film with 8 wt% of BN.

(Figures 4a and 4d). For BN/PEN, the SEM micrographs show that the BN is randomly dispersed on the surface of PEN matrix, indicating the poor compatibility between BN and PEN (Figures 4e and 4f). Meanwhile, the smooth surface of BN on the cross-section of BN/ PEN suggests that the BN/ PEN film is broken down on the interface of BN and PEN. The different dispersability and compatibility between BN and PEN in BN/ PEN and BN@SPEN/PEN should be attributed to those factors: (1) the BN aggregates in PEN matrix due to the different polarities and surface energies between the organic and inorganic phases (32); (2) the SPEN shell hinders the aggregation of BN; (3) the compatibility between the BN@SPEN and PEN matrix is much better than that between BN and PEN.

3.3 Rheological properties of BN@SPEN/PEN

Oscillatory shear rheological measurements were tested at 320°C to explore the relationship between BN and PEN. Figure 5 exhibits complex viscosity (η*) and storage modulus (G’) of the composite films at frequency ranging from 0.1 to 100 Hz. As shown in Figure 5a, G’ increases as BN@SPEN increasing, indicating the reinforcement effect of BN@SPEN. In the all range of frequency, G’ of PEN and PEN composites show similar changing behavior, suggesting that the BN@SPEN are well dispersed in the PEN matrix. In addition, G’ increases obviously at the low frequency when the BN@SPEN loading is higher than 12 wt%, indicating a sudden changing of property in the composites which would be resulted from the formation of percolation network (38). Figure 5b exhibits complex viscosity (η*) of BN@SPEN/PEN. Firstly, η* decreases gradually with increasing frequency, indicating the pseudoplastic fluid character of BN@SPEN/PEN. Secondly, η* increases with increment of BN@SPEN, which demonstrates BN@SPEN/PEN is much more rigid than PEN and acts as reinforce in the system.

Figure 5 (a) Dynamic storage modulus and (b) complex viscosity of PEN and BN@SPEN/PEN composite films obtained in dynamic frequency sweep from 0.10 to 100 rad/s at 320°C.
Figure 5

(a) Dynamic storage modulus and (b) complex viscosity of PEN and BN@SPEN/PEN composite films obtained in dynamic frequency sweep from 0.10 to 100 rad/s at 320°C.

3.4 Thermal properties of BN@SPEN/PEN

Figure 6 shows the DSC and TGA results of BN@SPEN/PEN composites. The glass transition temperatures (Tg) of PEN is 208°C. After the incorporation of BN@SPEN, the Tg of the BN@SPEN/PEN composites is almost the same (Table 1), indicating BN@SPEN does not influence the Tg of PEN matrix. In addition, the high Tg suggest high thermal stability of the BN@SPEN/PEN composites

Figure 6 (a) DSC curves of PEN and BN@SPEN/PEN composite films, (b) TGA curves of PEN and BN@SPEN/PEN composite films.
Figure 6

(a) DSC curves of PEN and BN@SPEN/PEN composite films, (b) TGA curves of PEN and BN@SPEN/PEN composite films.

Table 1

Thermal property of PEN and BN@SPEN/PEN composites.

BN@SPEN content0 wt%4 wt%8 wt%12 wt%16 wt%20 wt%
Tg (°C)208.1206.0206.2206.0205.2204.8
T5% (°C)517.0508.2499.0489.3480.0478.2
Tmax (°C)536.1526.0519.2510.3505.1502.0

which can be used at high temperature. Figure 6b depicts the TGA curves of the BN@SPEN/PEN composites. The 5 wt% and maximum weight-loss temperature (T5%) and (Tmax) of PEN used in this study are 517°C and 536°C, respectively (Table 1). The T5% and Tmax decrease slightly with the introduction of BN@SPEN. This is due to the lower decomposition temperature of SPEN of BN@SPEN. Nevertheless, the T5% of the composites is still higher than 470°C, indicating that the composites can be used at high temperature. In addition, the BN content in BN@SPEN/PEN composites is calculated according to the residual mass at 790°C on the TGA curves. The residual mass of PEN, BN@SPEN/PEN4, BN@SPEN/PEN8, BN@SPEN/PEN12, BN@SPEN/PEN16, andBN@SPEN/PEN20

at 790°C is 62.6%, 63.4%, 64.4%, 65.4%, 66.9%, and 67.7% respectively. Therefore, the BN@SPEN content in BN@SPEN/PEN composites is calculated to be 3.3, 7.5, 11.6, 17.8 and 21.1 wt% respectively. Accordingly, the BN content in BN@SPEN/PEN composites is calculated to be 2.4, 5.5, 8.5, 12.9 and 15.4 wt% respectively as the content of BN in BN@SPEN was calculated to be 72.6 wt%.

3.5 Mechanical properties of BN@SPEN/PEN

Mechanical properties of BN@SPEN/PEN composite films with varied mass BN@SPEN are shown in Figure 7. The tensile strength of the BN@SPEN/PEN composite films is presented in Figure 7a. From the illustration, the tensile strength of BN@SPEN/PEN increases as increasing mass fraction of SPEN@BN in the range of 0.0 to 8 wt%. Tensile strength decreases when mass fraction of BN@SPEN/PEN increasing to 12.0 wt%. The tensile modulus of the composite films shows the similar result as that of the tensile strength (Figure 7a, Table 2). Besides, Figure 7b shows the influence of BN@SPEN particles on the breaking elongation of the composite films. It can be seen that elongation at break of the pure film is 10.6% (Table 2). After the incorporation of BN@SPEN particles, there is a trend that the elongation at break decreases with the increasing BN@SPEN mass fraction, which is attributed to the incorporation of BN@SPEN.

Figure 7 Mechanical properties of PEN and BN@SPEN/PEN composite films: (a) tensile strength and tensile modulus (b) elongation at break.
Figure 7

Mechanical properties of PEN and BN@SPEN/PEN composite films: (a) tensile strength and tensile modulus (b) elongation at break.

Table 2

Mechanical properties of PEN and BN@SPEN/PEN composites.

BN@SPEN content0 wt%4 wt%8 wt%12 wt%16 wt%20 wt%
Tensile strength (MPa)94.196.2104.185.680.878.1
Tensile modulus (MPa)248924332517240023602301
Elongation at break (%)10.69.89.18.98.28.0

3.6 Coefficients of thermal expansion of BN@SPEN/PEN

High coefficient of thermal expansion (CTE) indicates poor dimensional stability and low reliability of the material during its application (39). Therefore, CTE of the materials

plays a significant role in its application. DMA was employed to investigate CTE of PEN and BN@SPEN/PEN composite. CTE values of the BN@SPEN/PEN composites are shown in Figure 8. The CTE of PEN is as high as 0.85 μm/°C. The CTE decreases to 0.65 μm/°C for BN@SPEN/PEN4 with 4 wt% of BN@SPEN. With the addition of BN@SPEN, the CTE is further reduced, and when used weight of BN@SPEN is 20 wt%, the CTE is as low as 0.35 μm/°C. The well-dispersed BN@SPEN obstruct expansion of PEN chains when temperature arises, which lessen CTE value for the BN@SPEN/PEN composites.

Figure 8 Coefficient of thermal expansion values of BN@SPEN/PEN composite films.
Figure 8

Coefficient of thermal expansion values of BN@SPEN/PEN composite films.

3.7 Thermal conductivity of BN@SPEN/PEN

Figure 9 shows the thermal conductivity of PEN incorporated with different mass fraction of BN@SPEN. Usually, most of the organic polymers are thermal insulators. The thermal conductivity (TC) of PEN is 0.29 W/(m⋅K), as shown in Figure 9. The results indicate that the addition of BN@SPEN into the polymer matrix increases the thermal conductivity value of PEN composite films obviously. When the BN@SPEN content is 4 wt%, the TC of the BN@SPEN/PEN reaches 0.35 W/(m⋅K), with an improvement of 21%. When 20 wt% of BN@SPEN is incorporated, the TC of the BN@SPEN/PEN20 is as high as 0.69 W/(m⋅K), which corresponds to 2.4 fold to that of PEN. In comparing with the composites incorporated with pristine BN (40, 41, 42), the thermal conductivity of the

Figure 9 Thermal conductivity of BN@SPEN/PEN composite films.
Figure 9

Thermal conductivity of BN@SPEN/PEN composite films.

BN@SPEN/PEN is improved much more obviously at the same content of BN. This is mainly ascribed to the fact that the addition of BN@SPEN effectually minimizes interfacial thermal contact resistance between the PEN and BN. Besides, BN@SPEN serve as conductive channels improving the transportation of thermal phonons of PEN composites.

4 Conclusions

In this article, novel BN@SPEN/PEN composites with PEN as substrate and BN@SPEN as reinforcement were fabricated. BN@SPEN was obtained by ultrasonic method combined with the post-treatment bonding process. The results of FTIR, TGA, SEM and TEM showed the successful coating of BN micro-platelets using the SPEN. The SEM observation and rheology measurement showed that the compatibility between the BN@SPEN and PEN matrix was much better than that between BN and PEN. BN@SPEN/PEN films showed excellent thermal property with Tg exceeding 200°C and T5% higher than 470°C. Mechanical properties investigation manifested that the BN@SPEN/PEN exhibited superior mechanical properties (tensile strength and Young’s modulus higher than 78 MPa and 2300 MPa respectively). Thermal conductivity of BN@SPEN/PEN films was increased to 0.69 W/(m⋅K) at 20 wt% content of BN@SPEN, showing a 138% increasement comparing with pure PEN.

Tel. /fax: +86-28-83207326.
#Renbo Wei and Qian Xiao contributed equally to this work.

Acknowledgements

The authors wish to thank for financial supports of this work from the National Natural Science Foundation of China (Project No. 51603029 and 51773028), China Postdoctoral Science Foundation (2017M623001) and National Postdoctoral Program for Innovative Talents (Project No. BX201700044).

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Received: 2018-07-17
Accepted: 2018-08-22
Published Online: 2019-05-08

© 2019 Wei et al., published by De Gruyter

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

Artikel in diesem Heft

  1. Special Issue: Polymers and Composite Materials / Guest Editor: Esteban Broitman
  2. A novel chemical-consolidation sand control composition: Foam amino resin system
  3. Bottom fire behaviour of thermally thick natural rubber latex foam
  4. Preparation of polymer–rare earth complexes based on Schiff-base-containing salicylic aldehyde groups attached to the polymer and their fluorescence emission properties
  5. Study on the unsaturated hydrogen bond behavior of bio-based polyamide 56
  6. Effect of different nucleating agent on crystallization kinetics and morphology of polypropylene
  7. Effect of surface modifications on the properties of UHMWPE fibres and their composites
  8. Thermal degradation kinetics investigation on Nano-ZnO/IFR synergetic flame retarded polypropylene/ethylene-propylene-diene monomer composites processed via different fields
  9. Properties of carbon black-PEDOT composite prepared via in-situ chemical oxidative polymerization
  10. Regular articles
  11. Polyarylene ether nitrile and boron nitride composites: coating with sulfonated polyarylene ether nitrile
  12. Influence of boric acid on radial structure of oxidized polyacrylonitrile fibers
  13. Preparing an injectable hydrogel with sodium alginate and Type I collagen to create better MSCs growth microenvironment
  14. Application of calcium montmorillonite on flame resistance, thermal stability and interfacial adhesion in polystyrene nanocomposites
  15. Modifications of microcrystalline cellulose (MCC), nanofibrillated cellulose (NFC), and nanocrystalline cellulose (NCC) for antimicrobial and wound healing applications
  16. Polycation-globular protein complex: Ionic strength and chain length effects on the structure and properties
  17. Improving the flame retardancy of ethylene vinyl acetate composites by incorporating layered double hydroxides based on Bayer red mud
  18. N, N’-sebacic bis(hydrocinnamic acid) dihydrazide: A crystallization accelerator for poly(L-lactic acid)
  19. The fabrication and characterization of casein/PEO nanofibrous yarn via electrospinning
  20. Waterborne poly(urethane-urea)s films as a sustained release system for ketoconazole
  21. Polyimide/mica hybrid films with low coefficient of thermal expansion and low dielectric constant
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  23. Stimuli-responsive DOX release behavior of cross-linked poly(acrylic acid) nanoparticles
  24. Continuous fabrication of near-infrared light responsive bilayer hydrogel fibers based on microfluidic spinning
  25. A novel polyamidine-grafted carboxymethylcellulose: Synthesis, characterization and flocculation performance test
  26. Synthesis of a DOPO-triazine additive and its flame-retardant effect in rigid polyurethane foam
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  31. Preparation of rosin-based polymer microspheres as a stationary phase in high-performance liquid chromatography to separate polycyclic aromatic hydrocarbons and alkaloids
  32. Effects of chemical modifications on the rheological and the expansion behavior of polylactide (PLA) in foam extrusion
  33. Enhanced thermal conductivity of flexible h-BN/polyimide composites films with ethyl cellulose
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  40. Voigt-based swelling water model for super water absorbency of expanded perlite and sodium polyacrylate resin composite materials
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  43. A glimpse of biodegradable polymers and their biomedical applications
  44. Development of vegetable oil-based conducting rigid PU foam
  45. Conetworks on the base of polystyrene with poly(methyl methacrylate) paired polymers
  46. Effect of coupling agent on the morphological characteristics of natural rubber/silica composites foams
  47. Impact and shear properties of carbon fabric/ poly-dicyclopentadiene composites manufactured by vacuum‐assisted resin transfer molding
  48. Effect of resins on the salt spray resistance and wet adhesion of two component waterborne polyurethane coating
  49. Modifying potato starch by glutaraldehyde and MgCl2 for developing an economical and environment-friendly electrolyte system
  50. Effect of curing degree on mechanical and thermal properties of 2.5D quartz fiber reinforced boron phenolic composites
  51. Preparation and performance of polypropylene separator modified by SiO2/PVA layer for lithium batteries
  52. A simple method for the production of low molecular weight hyaluronan by in situ degradation in fermentation broth
  53. Curing behaviors, mechanical properties, dynamic mechanical analysis and morphologies of natural rubber vulcanizates containing reclaimed rubber
  54. Developing an epoxy resin with high toughness for grouting material via co-polymerization method
  55. Application of antioxidant and ultraviolet absorber into HDPE: Enhanced resistance to UV irradiation
  56. Study on the synthesis of hexene-1 catalyzed by Ziegler-Natta catalyst and polyhexene-1 applications
  57. Fabrication and characterization of conductive microcapsule containing phase change material
  58. Desorption of hydrolyzed poly(AM/DMDAAC) from bentonite and its decomposition in saltwater under high temperatures
  59. Synthesis, characterization and properties of biomass and carbon dioxide derived polyurethane reactive hot-melt adhesives
  60. The application of a phosphorus nitrogen flame retardant curing agent in epoxy resin
  61. High performance polyimide films containing benzimidazole moieties for thin film solar cells
  62. Rigid polyurethane/expanded vermiculite/ melamine phenylphosphate composite foams with good flame retardant and mechanical properties
  63. A novel film-forming silicone polymer as shale inhibitor for water-based drilling fluids
  64. Facile droplet microfluidics preparation of larger PAM-based particles and investigation of their swelling gelation behavior
  65. Effect of salt and temperature on molecular aggregation behavior of acrylamide polymer
  66. Dynamics of asymmetric star polymers under coarse grain simulations
  67. Experimental and numerical analysis of an improved melt-blowing slot-die
https://doi.org/10.1515/epoly-2019-0009
Schlagwörter für diesen Artikel
polyarylene ether nitrile; boron nitride; surface coating; sulfonated polyarylene ether nitrile
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Special Issue: Polymers and Composite Materials / Guest Editor: Esteban Broitman
  2. A novel chemical-consolidation sand control composition: Foam amino resin system
  3. Bottom fire behaviour of thermally thick natural rubber latex foam
  4. Preparation of polymer–rare earth complexes based on Schiff-base-containing salicylic aldehyde groups attached to the polymer and their fluorescence emission properties
  5. Study on the unsaturated hydrogen bond behavior of bio-based polyamide 56
  6. Effect of different nucleating agent on crystallization kinetics and morphology of polypropylene
  7. Effect of surface modifications on the properties of UHMWPE fibres and their composites
  8. Thermal degradation kinetics investigation on Nano-ZnO/IFR synergetic flame retarded polypropylene/ethylene-propylene-diene monomer composites processed via different fields
  9. Properties of carbon black-PEDOT composite prepared via in-situ chemical oxidative polymerization
  10. Regular articles
  11. Polyarylene ether nitrile and boron nitride composites: coating with sulfonated polyarylene ether nitrile
  12. Influence of boric acid on radial structure of oxidized polyacrylonitrile fibers
  13. Preparing an injectable hydrogel with sodium alginate and Type I collagen to create better MSCs growth microenvironment
  14. Application of calcium montmorillonite on flame resistance, thermal stability and interfacial adhesion in polystyrene nanocomposites
  15. Modifications of microcrystalline cellulose (MCC), nanofibrillated cellulose (NFC), and nanocrystalline cellulose (NCC) for antimicrobial and wound healing applications
  16. Polycation-globular protein complex: Ionic strength and chain length effects on the structure and properties
  17. Improving the flame retardancy of ethylene vinyl acetate composites by incorporating layered double hydroxides based on Bayer red mud
  18. N, N’-sebacic bis(hydrocinnamic acid) dihydrazide: A crystallization accelerator for poly(L-lactic acid)
  19. The fabrication and characterization of casein/PEO nanofibrous yarn via electrospinning
  20. Waterborne poly(urethane-urea)s films as a sustained release system for ketoconazole
  21. Polyimide/mica hybrid films with low coefficient of thermal expansion and low dielectric constant
  22. Effects of cylindrical-electrode-assisted solution blowing spinning process parameters on polymer nanofiber morphology and microstructure
  23. Stimuli-responsive DOX release behavior of cross-linked poly(acrylic acid) nanoparticles
  24. Continuous fabrication of near-infrared light responsive bilayer hydrogel fibers based on microfluidic spinning
  25. A novel polyamidine-grafted carboxymethylcellulose: Synthesis, characterization and flocculation performance test
  26. Synthesis of a DOPO-triazine additive and its flame-retardant effect in rigid polyurethane foam
  27. Novel chitosan and Laponite based nanocomposite for fast removal of Cd(II), methylene blue and Congo red from aqueous solution
  28. Enhanced thermal oxidative stability of silicone rubber by using cerium-ferric complex oxide as thermal oxidative stabilizer
  29. Long-term durability antibacterial microcapsules with plant-derived Chinese nutgall and their applications in wound dressing
  30. Fully water-blown polyisocyanurate-polyurethane foams with improved mechanical properties prepared from aqueous solution of gelling/ blowing and trimerization catalysts
  31. Preparation of rosin-based polymer microspheres as a stationary phase in high-performance liquid chromatography to separate polycyclic aromatic hydrocarbons and alkaloids
  32. Effects of chemical modifications on the rheological and the expansion behavior of polylactide (PLA) in foam extrusion
  33. Enhanced thermal conductivity of flexible h-BN/polyimide composites films with ethyl cellulose
  34. Maize-like ionic liquid@polyaniline nanocomposites for high performance supercapacitor
  35. γ-valerolactone (GVL) as a bio-based green solvent and ligand for iron-mediated AGET ATRP
  36. Revealing key parameters to minimize the diameter of polypropylene fibers produced in the melt electrospinning process
  37. Preliminary market analysis of PEEK in South America: opportunities and challenges
  38. Influence of mid-stress on the dynamic fatigue of a light weight EPS bead foam
  39. Manipulating the thermal and dynamic mechanical properties of polydicyclopentadiene via tuning the stiffness of the incorporated monomers
  40. Voigt-based swelling water model for super water absorbency of expanded perlite and sodium polyacrylate resin composite materials
  41. Simplified optimal modeling of resin injection molding process
  42. Synthesis and characterization of a polyisocyanide with thioether pendant caused an oxidation-triggered helix-to-helix transition
  43. A glimpse of biodegradable polymers and their biomedical applications
  44. Development of vegetable oil-based conducting rigid PU foam
  45. Conetworks on the base of polystyrene with poly(methyl methacrylate) paired polymers
  46. Effect of coupling agent on the morphological characteristics of natural rubber/silica composites foams
  47. Impact and shear properties of carbon fabric/ poly-dicyclopentadiene composites manufactured by vacuum‐assisted resin transfer molding
  48. Effect of resins on the salt spray resistance and wet adhesion of two component waterborne polyurethane coating
  49. Modifying potato starch by glutaraldehyde and MgCl2 for developing an economical and environment-friendly electrolyte system
  50. Effect of curing degree on mechanical and thermal properties of 2.5D quartz fiber reinforced boron phenolic composites
  51. Preparation and performance of polypropylene separator modified by SiO2/PVA layer for lithium batteries
  52. A simple method for the production of low molecular weight hyaluronan by in situ degradation in fermentation broth
  53. Curing behaviors, mechanical properties, dynamic mechanical analysis and morphologies of natural rubber vulcanizates containing reclaimed rubber
  54. Developing an epoxy resin with high toughness for grouting material via co-polymerization method
  55. Application of antioxidant and ultraviolet absorber into HDPE: Enhanced resistance to UV irradiation
  56. Study on the synthesis of hexene-1 catalyzed by Ziegler-Natta catalyst and polyhexene-1 applications
  57. Fabrication and characterization of conductive microcapsule containing phase change material
  58. Desorption of hydrolyzed poly(AM/DMDAAC) from bentonite and its decomposition in saltwater under high temperatures
  59. Synthesis, characterization and properties of biomass and carbon dioxide derived polyurethane reactive hot-melt adhesives
  60. The application of a phosphorus nitrogen flame retardant curing agent in epoxy resin
  61. High performance polyimide films containing benzimidazole moieties for thin film solar cells
  62. Rigid polyurethane/expanded vermiculite/ melamine phenylphosphate composite foams with good flame retardant and mechanical properties
  63. A novel film-forming silicone polymer as shale inhibitor for water-based drilling fluids
  64. Facile droplet microfluidics preparation of larger PAM-based particles and investigation of their swelling gelation behavior
  65. Effect of salt and temperature on molecular aggregation behavior of acrylamide polymer
  66. Dynamics of asymmetric star polymers under coarse grain simulations
  67. Experimental and numerical analysis of an improved melt-blowing slot-die
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