γ-射线辐照法制备HDPE/PA6阻隔性材料及其性能研究

研究了富氧气氛中高密度聚乙烯(HDPE)的γ-射线辐照氧化及其与尼龙-6(PA6)的共混增容和共混材料的阻隔性能.FT-IR测试结果表明, 经γ-射线辐照的HDPE与PA6发生了化学反应或产生了弱相互作用.SEM照片显示4γHDPE (4h辐照,66Gy/min)与PA6具有良好的相容性,PA6在共混体系中呈层状分布.共混材料的阻隔性能测试结果表明4γHDPE/PA6共混物对二甲苯的阻隔性较HDPE/PA6共混物有明显提高.力学性能测试显示4γHDPE/PA6共混物力学性能优良.     

γ—射线辐照法制备HDPE／PA6辐隔性材料及其性能研究

研究了富氧气氛中高密度聚乙烯（HDPE）的γ－射线辐照氧化及其与尼龙－6(PA6)原共混增容和共混材料的阻隔性能。FT－IR测试结果表明，经γ－射线辐照的HDPE与PA6发生了化学反应或产生了弱相互作用。SEM照片显示4γHDPE（4h辐照，66Gy/min)与PA6具有良好的相容性，PA6在共混体系中呈层状分布。共混材料的阻隔性能测试结果表明4γHDPE／PA6共混物对二甲苯的阻隔性能HDPE／PA6共混物有明显提高。力学性能测试显示4γHDPE／PA6共混物力学性能优良。     

γ-射线辐照HDPE与PA－6共混物的结构与其对二甲苯阻隔性能的关系

高密度聚乙烯;尼龙-6;相结构;γ-射线辐照HDPE与PA－6共混物的结构与其对二甲苯阻隔性能的关系     

聚酰胺6/蒙脱石纳米复合材料的紫外光老化

聚合物 /层状硅酸盐纳米复合材料的研究十分活跃 [1～ 4 ] .聚酰胺 6/蒙脱石 ( PA6/MMT)纳米复合材料与纯聚酰胺 6( PA6)相比 ,模量和强度明显提高 ,耐热性能提高尤为显著 .光氧化行为材料科学领域的重要研究课题 .Admas等 [5]报道在紫外光照射下 ,聚丙烯 /粘土纳米复合材料的氧化速度要比纯聚丙烯的快 .对于 PA6/MMT纳米复合材料的光老化研究尚未见报道 .本文以傅里叶变换红外光谱定量研究手段 ,对比分析了 PA6/MMT纳米复合材料与 PA6的紫外光氧化性能 .1　实验部分　　采用熔体插层技术 ,将 PA6( Honeywell B1 0 0 MP)和有机蒙…     

SMA/蒙脱石纳米复合材料增容PA6/ABS共混体系

采用原位插层法制备苯乙烯-马来酸酐交替共聚物/蒙脱石(SMA/MMT)纳米复合材料增容PA6/ABS共混体系,并与SMA及MMT的增容效果进行比较,运用TEM、SEM、DSC及XRD研究了增容剂SMA/MMT及MMT的增容机理.结果表明,采用SMA做增容剂,体系机械性能下降;MMT可使体系拉伸强度提高,但冲击强度下降;采用SMA/MMT纳米复合材料做为增容剂,可提高共混体系的强度及韧性.TEM、XRD、DSC及SEM研究结果表明,PA6/ABS/(SMA-MMT)体系中MMT主要分布于两相界面处,ABS及PA6分子链可进入MMT层间,形成类似于共聚物结构,起到增容剂的作用,从而降低分散相粒径,增加两相界面作用力,有利于体系力学性能的提高.PA6/ABS/MMT体系中MMT主要分布于连续相PA6中,虽然对分散相粒径影响较小,但增强了PA6相强度,使得体系力学性能提高.     

聚甲醛和尼龙12共混物的微观结构与力学性能

采用SEM、FT-IR、DSC、WAXD等方法对POM/PA12共混物的微观结构进行分析,并测试其力学性能,结果表明,在POM/PA12共混物中,存在着氢键的相互作用.PA12的加入,使POM的熔点下降,共混物的微晶尺寸入L₁₁₀及晶胞参数有所增大.微晶尺寸L₁₁₀在10.87¹4.89nm之间时,PA12对POM具有增韧改性作用.     

sPS/PA6/蒙脱土纳米复合材料的制备与性能

讨论了间规聚苯乙烯 (sPS) 尼龙 6(PA6) 磺化间规聚苯乙烯 (SsPS H) 蒙脱土纳米复合材料的制备技术和新材料的结构与性能特征 .蒙脱土经层间改性处理后 (MTN) ,可分别将SsPS H和aPS(无规聚苯乙烯 )插入其纳米层间 ,制备出插层型纳米复合物MTN SsPS和MTN aPS .在sPS/PA6/SsPS H三组分共混体系中加入MTN SsPS或MTN aPS ,进行四组分熔融共混即可制备出sPS/PA6/SsPS H/蒙脱土纳米复合材料 .TEM测定证实了蒙脱土在基体中的层厚分布约为 5 0nm .此外 ,采用DSC、DMA、XRD及力学性能测试仪等现代分析方法对sPS/PA6/SsPS H/蒙脱土纳米复合材料的结构与性能进行了详细研究 .研究结果表明这种纳米复合材料具有优良的综合性能     

聚苯胺/蒙脱土纳米复合材料的制备及吸波性能研究

以十二烷基苯磺酸(DBSA)作为乳化剂和掺杂剂,通过乳液聚合的方法制备了DBSA掺杂聚苯胺/蒙脱土(PANI-DBSA/MMT)纳米复合物,并对其微波吸收特性进行了研究.通过X射线衍射(XRD)、傅立叶红外(FT-IR)和四探针测试仪对复合物进行了初步表征.结果表明,PANI-DBSA/MMT复合物中MMT层间距离明显扩大,纳米复合物中的PANI以emeraldine盐的形式存在,是一种典型的插层型纳米复合物.利用HP8722ES矢量网络分析仪测量了2 mm厚、PANI-DBSA/MMT含量为50 wt%的试样在2.0~18 GHz的复介电常数和复磁导率,经计算得到以反射损耗表示的微波吸收曲线,发现PANI-DBSA/MMT纳米复合物在9.1~12.5 GHz范围内反射损耗小于-10 dB,在11 GHz处存在的最大反射损耗为-15.8 dB.     

纳米Ag/CNTs复合材料的制备、表征及对环三亚甲基三硝胺热分解的影响

采用银镜法和水热法制备了两种纳米Ag/CNTs(碳纳米管)复合材料, 利用傅里叶变换红外(FTIR)光谱、粉末X射线衍射(XRD)、透射电子显微镜(TEM)、扫描电子显微镜及能量散射光谱仪(SEM-EDS)对复合物的物相、组成、形貌和结构进行分析表征, 并运用差示扫描量热法(DSC)研究了纳米Ag/CNTs 复合材料对环三亚甲基三硝胺(RDX)热分解特性的影响. 结果表明: 纳米Ag 以10-80 nm的不规则球形“粘附”于纳米CNTs 表面,分散较均匀, 水热法制得的复合物表面纳米Ag较大、且负载的Ag粒子较多; 纳米Ag/CNTs 复合材料的加入改变了RDX的热分解过程, 使原有占主导的液相分解变为二次的气相反应加剧, RDX主分解峰形发生了明显的改变; 纳米Ag/CNTs 复合材料对RDX热分解的催化主要表现为分解温度的降低.     

Mn_3O_4/氧化石墨烯纳米复合物的制备及其超级电容性能

利用锰前驱体与氧化石墨烯(GO)原位反应制备了Mn3O4/GO纳米复合物超级电容器电极材料;采用扫描电镜、透射电镜及X射线衍射仪分析了纳米复合物的形貌和结构;并利用交流阻抗分析及充放电测试测定了纳米复合材料的电化学性质和电容性质.结果表明,引入氧化石墨烯可增强纳米复合物的导电性及稳定性,提高Mn3O4的电容特性,从而使得纳米复合物具有较高的比电容(350F/g)和较长的循环寿命(超过1 000次).     

Photo-oxidation behaviour of polyethylene/polyamide 6 blends filled with organomodified clay: Improvement of the photo-resistance through morphology modification

The impact of small amounts of organomodified clay (OMMT) on the photo-degradation behaviour of two blends obtained by mixing either low-density polyethylene (LDPE) or high density polyethylene (HDPE) with polyamide 6 (PA6) (LDPE/PA6 and HDPE/PA6 75/25 wt-%) was studied. The complex photo-degradation behaviour was followed by monitoring the main physical-mechanical properties of the blends. In particular, mechanical and spectroscopic tests were performed in conditions of accelerated artificial aging. An accurate mechanical and morphological characterization was previously carried out. The presence of the OMMT promotes the unexpected formation of a co-continuous morphology for the HDPE/PA6 blend without significantly improving the interfacial adhesion. Differently, the OMMT-filled LDPE/PA6 blend exhibits a finely distributed morphology, and some apparent improvement of the interfacial adhesion was noticed. Probably due to these differences in microstructure, a different impact of the nanoparticles on the photo-resistance behaviours was observed for the two families of samples. In particular, the HDPE-based nanocomposite blend exhibits an improved photo-resistance, while the opposite occurs for the LDPE-based system.     

Friction and wear mechanisms of polyamide 66/high density polyethylene blends

Polyamide 66 (PA66)/high density polyethylene (HDPE) blends having miscible structure were produced by compatibilization of HDPE grafted with maleic anhydride (HDPE‐g‐MAH). Mechanical and tribological properties of blends in different compositions were tested. It was found that the polymer blends greatly improved the mechanical properties of PA66 and HDPE. Blending HDPE with PA66 significantly decreased the friction coefficient of PA66; the friction coefficients of blends with different compositions were almost the same and approximately equal to that of pure HDPE; the blends with 80 vol % PA66 exhibited the best wear resistance. The transfer films, counterpart surfaces, and wear debris formed during sliding were investigated by Scanning Electron Microscopy (SEM), and Differential Scanning Calorimetry (DSC) analysis was further carried out on wear debris. These investigations indicated that the thermal control of friction model is applicable to PA66/HDPE blend, that is the friction coefficient of blend is governed by the HDPE component, which possesses a lower softening point relative to the PA66 component in this system. The wear mechanism of PA66/HDPE blend transforms from PA66 to HDPE as the HDPE content increases. PA66, as the component with higher softening point, increases the hardness of blend, enhances the ability of blend to form a transfer film on the counterface, and inhibits the formation of larger belt‐like debris of HDPE, at the same time, the presence of self‐lubricating HDPE in the system decreases the friction coefficient and the frictional heat, all of these factors are favorable for the wear resistance of PA66/HDPE blend. © 2005 Wiley Periodicals, Inc. J Polym Sci Part B: Polym Phys 43: 2514–2523, 2005     

Co‐continuous Polyamide 6 (PA6)/Acrylonitrile‐Butadiene‐Styrene (ABS) Nanocomposites

Summary: Polyamide 6 (PA6)/acrylonitrile‐butadiene‐styrene (ABS) (40/60 w/w) nanocomposites with a novel morphology were prepared by the melt mixing of PA6, ABS and organoclay. The blend nanocomposites had a co‐continuous structure, in which both PA6 and styrene‐acrylonitrile (SAN) were continuous phases. It was found that the toughening rubber particles were only located in the SAN phase and the strengthening clay platelets were selectively dispersed in the PA6 phase. The co‐continuous nanocomposites showed greatly improved mechanical properties over the whole temperature range when compared with the same blend sample without clay.

Schematic diagram for the co‐continuous ABS/PA6 blend nanocomposite.     

Maleic Anhydride Polyethylene Octene Elastomer Toughened Polyamide 6/Polypropylene Nanocomposites: Mechanical and Morphological Properties

A series of polyamide 6/polypropylene (PA6/PP) blends and nanocomposites containing 4 wt% of organophilic modified montmorillonite (MMT) were designed and prepared by melt compounding followed by injection molding. Maleic anhydride polyethylene octene elastomer (POEgMAH) was used as impact modifier as well as compatibilizer in the blend system. Three weight ratios of PA6/PP blends were prepared i.e. 80:20, 70:30, and 60:40. The mechanical properties of PA6/PP blends and nanocomposite were studied through flexural and impact properties. Scanning electron microscopy (SEM) was used to study the microstructure. The incorporation of 10 wt% POEgMAH into PA6/PP blends significantly increased the toughness with a corresponding reduction in strength and stiffness. However, on further addition of 4 wt% organoclay, the strength and modulus increased but with a sacrifice in impact strength. It was also found that the mechanical properties are a function of blend ratio with 70:30 PA6/PP having the highest impact strength, both for blends and nanocomposites. The morphological study revealed that within the blend ratio studied, the higher the PA6 content, the finer were the POEgMAH particles.     

Preparation and characterization of a novel nanocomposite particles via in situ emulsion polymerization of vinyl functionalized silica nanoparticles and vinyl acetate

A new class of poly(vinyl acetate) (PVAc)/silica nanocomposite particles was successfully prepared in aqueous solution through a facile synthetic process. First, vinyl functionalized silica nanoparticles (VFSs) were synthesized using one-step method in aqueous emulsion, and then the vinyl groups located on the surface of VFSs were used to induced in situ polymerization of vinyl acetate. Scanning electron microscopy (SEM) images showed that VFSs and PVAc/silica nanocomposite particles all revealed highly monodispersed and uniform spheres. Especially, PVAc/silica nanocomposite particles obtained from transmission electron microscopy images presented an obvious core–shell structure, and the thickness of PVAc shell grafting on the surface of VFSs core was about 17 nm. In addition, the influence of the hydrolyzed and condensed time of vinyl triethoxysilane on the size and size distribution of VFSs was also investigated. The results of dynamic light scattering and SEM analysis indicated that the size and size distribution of VFSs decreased gradually with the extension of the reaction time from 6 to 48 h. Moreover, the structures and thermal properties of the samples were characterized via FT-IR and heat-flow DSC–TG.     

Cocontinuous morphology of immiscible high density polyethylene/polyamide 6 blend induced by multiwalled carbon nanotubes network

The effect of functionalized multiwalled carbon nanotubes (FMWCNTs) on the phase morphology of immiscible high density polyethylene/polyamide 6 (HDPE/PA6, 50/50) blend has been investigated. Scanning electron microscopy (SEM) and transmission electron microscopy (TEM) were employed to study both the morphology variation of the nanocomposites and the selective distribution of FMWCNTs in the nanocomposites. It is clear that adding small amount of FMWCNTs (<2.0 wt.%) does not exert profound influence on the sea-island morphology of the nanocomposites. However, at moderate content of FMWCNTs (2.0 and 5.0 wt.%), a typical cocontinuous morphology is detected. Further increasing FMWCNTs content (10.0 wt.%) induces phase inversion. The crystallization behaviors of both HDPE and PA6 components were investigated by using differential scanning calorimetry (DSC) and wide angle X-ray diffraction (WAXD). The results show the apparent nucleation effect of FMWCNTs for PA6 crystallization due to the selective distribution of FMWCNTs in PA6 phase. Rheological measurements exhibit the presence of FMWCNTs network structure in the nanocomposites. It is suggested that the formation of the cocontinuous morphology and the novel crystallization behaviors of PA6 at high content of FMWCNTs are ascribed to the formation of the FMWCNTs network structure.     

Studies on the mechanical and friction properties of polyamide 6-Cu/Si nanocomposites

Polyamide 6 nanocomposites reinforced with Cu/Si nanoparticles (PA6-Cu/Si) were prepared by the in-situ ring-opening polymerization of ?-caprolactam. The in-situ polymerization was critical for preventing the aggregation of Cu/Si nanoparticles. The Cu/Si nanoparticles in the nanocomposite retained their nano characteristics and were not oxidized by the amino groups in PA6. The structure of the as-fabricated PA6-Cu/Si nanocomposite was evaluated by transmission electron microscopy (TEM), X-ray diffraction (XRD), and ultraviolet-visible absorption spectroscopy (UV-vis). The friction and wear resistance, mechanical strength, and antistatic performance of PA6-Cu/Si were also evaluated. The PA6 polymer chains prevent the Cu/Si nanoparticles from aggregation by coating the surface of the Cu/Si nanoparticles via physical adsorption or an electrostatic effect. The mass fraction of the Cu/Si nanoparticles also had a significant effect on the crystalline form of PA6. The γ crystalline form of PA6 was predominant at a high mass fraction of Cu/Si to PA6. Moreover, PA6-Cu/Si with improved mechanical properties and wear resistance was generated by tuning the amount of nano-Cu/Si filler added during the polymerization. PA6-Cu/Si with a nano-Cu/Si content of 0.5% possesses the highest tensile strength and wear resistance and shows promise in applications as a functional polymer-matrix composite.     

Largely enhanced ductility of immiscible high density polyethylene/polyamide 6 blends via nano‐bridge effect of functionalized multiwalled carbon nanotubes

Immiscible polymer blends usually exhibit negative deviation in mechanical properties compared with the corresponding pure polymers due to the weak interfacial bonding between the two polymers. Due to the bridge effect of the oriented carbon nanotubes (CNTs) on the craze and crack development at the load of stress, CNTs have been proved to be efficient toughening agent for polymers. In this work, functionalized multiwalled carbon nanotubes (FMWCNTs) have been introduced into immiscible high density polyethylene/polyamide 6 (HDPE/PA6) blends through different sample preparation methods. The mechanical measurements demonstrate that, when the nanocomposite is prepared from the HDPE master batch, the sample exhibits excellent tensile strength and toughness simultaneously. For all the nanocomposites, FMWCNTs tend to migrate and/or maintain in PA6 particles, leading to the variation of the crystallization behavior in PA6 phase. Further results based on morphologies characterization indicate that the intensified interfacial adhesion between HDPE and PA6, which is realized by the nano‐bridge effect of FMWCNTs in the interfaces, is the main reason for the largely improved ductility. Copyright © 2010 John Wiley & Sons, Ltd.     

Synthesis and Characterization of Polyindole/Poly(vinyl acetate) Conducting Composites

Composites of a polyindole (PIN) and poly(vinyl acetate) (PVAc) were prepared chemically using FeCl₃ as an oxidant agent in anhydrous media. The composite compositions were altered by varying the indole monomer during preparation. The composites were characterized by FTIR and UV‐visible spectroscopies, thermogravimetric analysis (TGA), differential scanning calorimetry (DSC), scanning electron microscopy (SEM), stress‐strain experiments and conductivity measurements. Moreover, the film of PVAc and PIN/PVAc composites were prepared by casting on glass Petri dishes to examine their stress‐strain properties. PIN/PVAc composites are thermally more stable than PIN. It was found that the conductivities of PIN/PVAc composites depend on the indole content in the composites.     

Characterization of PP/HDPE blend-based nanocomposites using different maleated polyolefins as compatibilizers

Nanocomposites based on a polypropylene (PP)/high density polyethylene (HDPE) blend were prepared using an organo-montmorillonite (15A) as a nano-filler and two maleated polyolefins (PE-MA and PP-MA) as compatibilizers. The phase morphology and typical physical properties of the prepared samples were examined. The nano-filler 15A was intercalated and/or partially exfoliated in the blend when PE-MA or PP-MA was present. The PE-MA facilitated the dispersibility of 15A to a better degree. The nano-filler 15A accelerated the crystallization of PP in the blends, whereas it hardly influenced the crystallization of HDPE. Moreover, at a slow cooling rate (i.e., 1 °C/min) the PP-MA induced a higher crystallization temperature for PP in the composite, while PE-MA impeded PP crystallization. On the other hand, the crystallization of HDPE in the composite was only slightly influenced by the presence of PE-MA or PP-MA. The thermal stability of PP/HDPE blend was enhanced after the addition of 15A regardless of the inclusion or not of PE-MA or PP-MA. The enhancement was more evident when the samples were scanned under an air environment than a N2 environment. The stiffness of PP/HDPE blend increased marginally after adding 15A and was slightly altered with the further inclusion of PP-MA. The presence of PE-MA in the composite caused a slight decline in the stiffness. The impact strength of PP/HDPE blend declined after the formation of nanocomposites, especially for the sample incorporating PP-MA.