层装分散形态聚合物合金

综述了层状分散形态聚合物合金的形态特征、材料选择、成型加工条件，以及层状分散形态聚合物的功能性。最后，综述了永久抗静电层状分散聚合物合金的制备及其应用进展。     

纳米粒子对聚合物的改性机理

无机纳米粒子对聚合物改性是近年来发展较快的方法之一，本文根据纳米粒子在聚合物中的形态，分别论述了具有链式结构、分散结构和层状结构的不同形态纳米粒子对聚合物的改性机理。     

熔融插层法制备聚合物/层状硅酸盐纳米复合材料的调控因素

综述了熔融插层法制备聚合物／层状硅酸盐纳米复合材料的调控因素，分析了插层过程中复合体系、加工工艺、热力学和动力学因素对聚合物插层与层状硅酸盐片层剥离分散的影响．并展望了聚合物／层状硅酸盐纳米复合材料的研究前景。     

粘土／塑料纳米复合技术及其应用的新发展

近年来，粘土（蒙脱土）剥离成纳米级厚度的层状硅酸盐并分散在聚合物基体中的粘土／塑料复合体系的制备技术发展很快，并在工程塑料、塑料包装等许多领域呈现出良好的应用前景。聚合物／层状硅酸盐纳米复合材料的结构、性能及应用等许多方面优于普通聚合物材料，是当今聚合物材料基础研究和应用开发的热点。     

高岭土复合材料的制备及其未来发展

高岭土是一类典型的层状硅酸盐矿物,层间距只有0.72nm,表面极性较大,与聚合物相容性很差,需要对其改性才能均匀地分散到聚合物中,均匀分散在聚合物中的高岭土可以有效地改善复合材料的机械性能、热性能等。~[2]     

具有自组装相形态的聚合物合金研究进展

详细介绍了两类具有自组装相形态的聚合物合金体系,即两分散相能形成核-壳结构分布于连续相中的三元不相容聚合物合金以及添加有固体纳米粒子的二元不相容聚合物混合物,讨论了前者的相形态及其影响因素和后者的相形态自组装行为及其影响因素。     

聚合物/层状硅酸盐纳米复合材料

聚合物/层状硅酸盐(PLS)纳米复合材料是近10年迅速发展起来的新交叉科学.由于聚合物纳米复合材料具有常规聚合物复合材料所没有的结构、形态以及较常规聚合物复合材料更优异的物理力学性能、耐热性和气体液体阻隔性能等,因而显示出重要的科学意义和应用前景.综述了聚合物/层状硅酸盐纳米复合材料的制备、结构表征、性能和应用情况,最后展望了其应用前景.     

聚合物─层状粘土矿物纳米复合材料的合成与表征

利用某些层状粘土矿物的吸附性、离子交换性和膨胀性，可以将一些聚合物单体嵌入到粘土矿物的层间，接着在受约束的二维层间域进行聚合，或者是将聚合物直接嵌入到它们的层间域，形成性能优异的聚合物—层状粘土矿物纳米复合材料和功能材料。本文简要地论述了2：1型层状粘土矿物的结构特点，聚合物—层状粘土矿物纳米复合材料的合成、表征及其性能。     

非层状纳米无机粒子/热塑性聚合物复合材料制备方法研究进展

纳米粒子由于十分容易聚集和团聚, 加之表面亲水性的纳米颗粒和表面憎水性的聚合物基体的相容性较差, 往往以较大的团聚体形式分散于聚合物基体树脂中, 导致复合材料的性能不佳。基于常规共混法的纳米颗粒/聚合物复合材料制备技术仍是重要的制备途径之一, 关键在于如何解决复合体系中纳米粒子的有效分散和利用问题。为此, 本文中针对非层状纳米无机粒子/热塑性聚合物复合材料的制备, 介绍了纳米无机粒子表面改性和纳米颗粒在热塑性聚合物中的分散技术方面的研究进展。      

低极性聚合物／层状硅酸盐纳米复合材料研究进展

针对低极性聚合物极性低，与极性的硅酸盐不相容的特点，综述了国内外制备高性能低极性聚合物／层状硅酸盐纳米复合材料的新方法，展望了低极性聚合物／层状硅酸盐的发展方向。     

HDPE／PET层状分散合金亚微相态与相容性关系

通过选择相容剂种类及添加量，改变了HDPE/PET共混体系中分散相的尺寸及形态从而获得了以PET为分散相的各种层状分散相态研究了共混体系相容性与相态之间的关系结果表明：PET层化趋势随体系的相容性增大而增强但当相容剂含量超过一定值时，层状分散相态从中心处开始被破坏．根据这一现象，提出了层化相容区的概念     

Preparation of composite dispersed phase morphologies in incompatible and compatible blends during melt processing

Most processing/morphology studies of multi-phase polymer blends have been concerned with controlling the size and shape of the dispersed phase. The dispersed phase is generally a pure homo- or copolymer (apart from low levels of interfacial modifier). This paper describes the preparation during melt processing of a complex polymer blend morphology known as a composite dispersed phase system. Microscopically this structure can be seen to be composed of three parts: two distinct phases with sub-inclusions within one of the phases. This system is a type of blend within a blend. Various microscopic techniques are used to show that a composite multi-phase morphology can be prepared in an incompatible polypropylene/ polycarbonate (PP/PC) blend as well as in a compatible polyethylene copolymer/polyamide blend. This structure has been generated at two compositions for polypropylene/ polycarbonate through melt blending. At 50% volume fraction (near the region of dual-phase continuity), simultaneous addition of components results in co-continuous polypropylene and polycarbonate phases with the latter containing small PP spherical sub-inclusions. At 25% PC (volume fraction) the generation of a composite dispersed phase in a polypropylene matrix is obtained by imposing phase inversion followed by controlling the mixing time. The morphology in this case consists of a polypropylene matrix, a polycarbonate dispersed phase and spherical polypropylene sub-inclusions within the dispersed polycarbonate. Partial stabilization of the composite morphology in incompatible blends with mixing time can be obtained through control of the viscosity of the dispersed phase. Polyethylene copolymer/polyamide blends have also been prepared by the phase inversion process and show that strong interfacial interactions between the polyamide sub-inclusions and polyethylene copolymer dispersed phase material results in complete stabilization of the composite dispersed phase morphology with very high retention of sub-inclusions persisting even after long mixing times.     

High-shear effects on the nano-dispersed structure of the PVDF/PA11 blends

The fabrication of miscible or nanostructured polymer blends or alloys raises much hope, but poses significant scientific and industrial challenges over the past several decades. Here, we propose a novel strategy using high-shear processing and demonstrate the high-shear effects on the nanodispersed structure formed in the poly(vinylidene fluoride) (PVDF)/polyamide 11 (PAll) blends, in which PA11 domains with a size of several tens of nanometers are dispersed in the PVDF phase. For the blend of PVDF/PA11 = 65/35, the TEM image shows that many nanometer-sized PAl1 particles are dispersed in the PVDF domain to form a special type of domain-in-domain morphology. In contrast, no PVDF nano-dispersion was observed in the PA11 phase. The effects of both the screw rotation speed and the mixing time on the blend structure were systematically studied. It shows that the extruder screw rotation speed and the mixing time are two critical factors to prepare the nanostructured blends. In addition, the investigations on the thermal behavior of the obtained blends indicate the improved miscibility between PVDF and PAl1 by the high shear processing.     

Effect of nanoclay and SEBS-g-MA on the morphology and properties of immiscible poly(methyl methacrylate)/polystyrene blend

In recent years, nanoclays are being used as compatibilizer for various immiscible polymer blends. However, little work has been done on the morphology of immiscible polymer blends in presence of both the nanoclay and a reactive compatibilizer. Here, we report the synergistic effect of nanoclay and SEBS-g-MA on the morphology and properties of (70/30 w/w) PMMA/PS blend. Scanning electron microscopy study of the blend with various amount of nanoclay and SEBS-g-MA indicated a reduction in the average domain sizes (D) of dispersed PS phase in PMMA matrix compared to that in the pure blend. Addition of both SEBS-g-MA and nanoclay significantly lowered the D of PS in the blend compared to that with only SEBS-g-MA or clay. X-ray diffraction study and transmission electron microscopy revealed the presence of intercalated clay platelets in PMMA matrix, as well as, at the interface of the (70/30 w/w) PMMA/PS blend-clay nanocomposites. Addition of SEBS-g-MA in the blend-clay nanocomposites promoted the exfoliation of clays in PMMA matrix. Thus, exfoliated clay platelets in PMMA matrix effectively restricted the coalescence of dispersed PS domains while SEBS-g-MA improved the adhesion between the phases at the interface. At certain loading (phr), storage modulus, elongation at break and thermal stability of the blend were greatly improved when both the nanoclay and SEBS-g-MA were present in the blend. The use of reactive compatibilizer and nanoclay in polymer blends may lead to a high performance material which combines the advantages of compatibilized polymer blends and the merits of polymer nanocomposites.     

聚合物共混物增容技术及发展

不混溶共混物的增容是迄今为止将相容性较差的多相聚合物共混物转化为高性能合金的最通用和最有效的方法。本文主要简述了增容的概念和其必要性以及聚合物在通过共混改性时所采用的各种增容手段:添加嵌段和接枝共聚物;添加反应性聚合物;添加低分子量化合物;添加功能纳米粒子等,并综述了不同增容方法的发展现状及增容作用对共混物的相形貌和最终性能(力学性能、热性能、电学性能等)的影响,并最后提出纳米粒子增容将成为共混物增容领域的热门方法,这种方法不仅起能到增容作用,还可以增加机械强度并且有可能给共混物带来新的性能。     

聚合物共混制备纳米和多孔碳纤维及性能研究

聚丙烯腈(PAN)和聚甲基丙烯酸甲酯(PMMA)共混膜的结构和尺寸可由两组分比例和分子量调整。以PAN为碳前驱体,PMMA为热分解聚合物,并控制m(PAN)/m(PMMA)为30/70和70/30,通过湿法纺丝制备了PAN/PMMA共混纤维。以m(PAN)/m(PMMA)为30/70和70/30的共混纤维为原丝经碳化后获得了纳米碳纤维(CNFs)和多孔碳纤维(PCFs)。利用扫描电镜观察了所得CNFs和PCFs的形貌,发现单根CNFs的直径为50～150nm,PCFs中孔的直径为0.1～1μm。由CNFs和PCFs的拉曼光谱分析了不同碳化温度对CNFs和PCFs石墨化程度的影响,结果表明随碳化温度升高,石墨化程度也增加,同时电导率也随之提高。     

PAN/PS共混超滤膜的制备及性能研究

采用共混法制备聚丙烯腈(PAN)/聚砜(PS)超滤膜,以聚丙烯腈作为第一组分(连续相),聚砜为第二组分(分散相),用相转化法流延成膜;研究共混比、聚合物浓度、添加剂、凝胶浴等对共混膜水通量和截留率的影响,并采用扫描电镜对膜的结构形态进行了观察。结果表明:PAN/PS共混膜与PAN膜具有相似的化学稳定性,但较PAN膜具有更好的分离透过性。     

聚合物共混初期形态结构发展的研究进展

就国外近期研究内容,介绍了熔融共混过程初期的形态结构发展模式。在聚合诉共混初期,分散相首先先形成片状物（带状物）,进而在剪切力场作用下碎裂成球形粒子,完全熔融以后,粒径变化很小;此模式对反应性体系和非反应性体系均适合。对于弹性体含量低的橡塑共混体系,在共混初期弹性粒子首先成为连续相,可用一“四阶段”相反转模式;对于反应性体系,此模式不会发迹但是相反转延迟发生,并伴有转矩增大现象。     

HDPE/MPA共混物层状结构及阻隔性能研究

将少量对烃类溶剂具有高效阻作用的阻隔性树脂－改性尼龙与高密度聚乙烯共混,通过对共混工艺条件和分散相ＭＰＡ形态的控制,可获得具有高阻性能的ＨＤＰＥ／ＭＰＡ共混材料。     

Thermal evolution of a silicone resin/polyurethane blend from preceramic to ceramic foam

Ceramic foams, prepared by the pyrolysis of a foamed blend of a methylsilicone preceramic polymer and a polyurethane, exhibit excellent mechanical properties. The thermal evolution of process to produce from the foamed blend (weight ratio of 1 to 1) to ceramic foam was investigated from room temperature to 1400°C. Firstly, the methylsilicone preceramic polymer was characterized with various techniques. Secondly, the weight decrease and the degradation gas from the unpyrolyzed foamed blend, the phase morphology change, the compositional change, and the dimensional change were investigated. The main variation of characteristics of the foamed blend was observed in the temperature range 400 to 600°C, where the largest weight loss occurred in TGA, for most of the measurements. At these temperatures, the decomposition of the polyurethane phase is mostly completed, and the polymer-to-ceramic conversion of the silicone resin is under way. The phase-morphological analysis surprisingly showed that the polyurethane was dispersed as particles in a methylsilicone preceramic polymer matrix, although originally polyurethane was intended to be used as a sacrificial template matrix. The polyurethane domain particles gradually aggregated and tended to disappear as the temperature increased, and the ceramic foam walls and struts appeared to be dense (for pyrolysis temperature <1400°C). These features can be explained assuming that the preceramic polymer matrix deformed during the decomposition of the polyurethane and the polymer-to-ceramic conversion.