尼龙6与半芳香性非晶尼龙原位共混物的结构与性能

一种半芳香的非晶尼龙共聚物溶解于熔融的己内酰胺中,引发后者负离子开环聚合原位制备尼龙6与非晶尼龙的共混物.与纯尼龙6相比较,此原位共混物的强度与模量显著提高.非晶区呈现单一的玻璃化转变,表明共混物为均相体系,其组分的相容性源于负离子聚合过程中链交换反应引起的共聚.与纯尼龙6相比较,此共混物的熔点与结晶度显著降低.此外,与纯尼龙6只存在α晶不同,共混物中伴生有大量的γ晶.当非晶尼龙含量为20 wt%时,绝大部分晶体为γ晶.然而,共混物中球晶仅有一定程度细化.共混物强度和模量的提高被认为主要源于非晶区分子活动能力降低以及γ晶相对含量的提高.     

微量聚四氢呋喃-聚甲基丙烯酸甲酯/聚四氢呋喃共混体系稀固体溶液中共聚物胶束的抑制成核作用

本工作将Leibler、Whitmore和Mayes等近期关于非晶嵌段共聚物共混体系胶束理论应用于结晶嵌段共聚物共混体系的熔融态,对聚甲基丙烯酸甲酯-聚四氢呋喃两嵌段共聚物与聚四氢呋喃均聚物共混体系的结晶行为进行了研究.结果表明,很低的共聚物浓度(如1％),其胶束在共混体系的结晶过程中即可显著地起到抑制成核的作用.这对改善结晶均聚物的形态及性能有一定的应用价值.     

尼龙1010结晶与熔融行为的研究

用DSC研究了降温速率R对尼龙10 10结晶与熔融的影响,以及室温(RT)和液氮(LN)骤冷退火样品的熔融.降温时结晶温度随R增大线性降低;T_g以上可完成结晶时结晶度相同;结晶起始温度>181℃生成的晶体有三个熔融峰,对应于环状和放射状球晶的转化与熔融;在181℃和T_g间结晶,无放射球晶转化峰;T_g下有结晶放热峰样品加热时有冷结晶发生.RT未退火样品三个熔融峰,退火温度T_α≥180℃样品两个峰,结晶度C∝T_a;LN未退火样品单一熔融峰,T_a>160℃双峰,T_a≤160℃三峰,低温峰温与C均∝T.     

微量聚四氢呋喃-聚甲基丙烯酸甲酯/聚四氢呋喃共混体系稀固体溶液中共聚物胶束的抑制成核作用

 本工作将Leibler、Whitmore和Mayes等近期关于非晶嵌段共聚物共混体系胶束理论应用于结晶嵌段共聚物共混体系的熔融态,对聚甲基丙烯酸甲酯-聚四氢呋喃两嵌段共聚物与聚四氢呋喃均聚物共混体系的结晶行为进行了研究.结果表明,很低的共聚物浓度(如1％),其胶束在共混体系的结晶过程中即可显著地起到抑制成核的作用.这对改善结晶均聚物的形态及性能有一定的应用价值.     

嵌段共聚物PVCH-b-PE-b-PVCH的多重结晶行为

通过采用差示扫描量热仪(DSC)主要研究了结晶-非晶嵌段共聚物聚乙烯基环己烷-b-聚乙烯-聚乙烯基环己烷(PVCH-b-PE-b-PVCH)溶液结晶样品的熔融与非等温再结晶过程.探讨了溶液结晶样品中微相分离结构的形成对嵌段共聚物受限结晶的影响,并发现样品在熔融后的非等温结晶过程中出现了多重结晶峰.通过对嵌段共聚物有序、...     

聚砜-尼龙6嵌段共聚体的溶液性质及其与聚砜、尼龙6均聚物的相容性的研究

<正> 我们曾在前二篇文章中指出非晶型双酚A聚砜(以下用B表示)与结晶形尼龙6(以下用N表示)经共混得到的共混物很脆,而聚砜-尼龙6嵌段共聚物(以下用B-N和N-B-N表示)却具有较B或N更优的耐溶剂性和耐水性,但是嵌段共聚物中B组分含量不能超过25％,这样就限制了材料的使用范围,然而由于B-N(或N-B-N)在同一分     

两性星形嵌段共聚物的结晶及络合性质

研究了聚苯乙烯(S)-聚环氧乙烷(E)星形嵌段共聚物的结晶及络合性质.结果表明,结晶度随E含量及分子量增大而增大.共聚物熔融后在20℃淬火比0℃淬火的结晶规整,氯仿溶液浇铸的样品比乙苯浇铸的规整.共聚物在甲苯溶液中呈现特殊的介晶现象.紫外吸收光谱表明,它能与苦味酸碱金属盐络合,使不溶于氯仿及甲苯的钾盐或钠盐进入溶液.     

乙丙共聚物及其共混物晶型探讨

用广角X-射线衍射(WAXD)和偏光显微镜(PLM)方法,研究了具有乙丙长序列乙丙共聚物及其共混物,发现通过熔融慢冷结晶样品,C_3含量在30mol％以上,衍射角2θ=20°处出现了属于γ-PP晶型的(140),(130)晶面衍射。含有乙丙长序列链结构的乙丙共聚物及共混物属(α+γ)混晶结构;含乙丙长序列的EPR以γ-相为主,嵌段物和共混物则以α-PP为主,形成γ-PP结构的必要条件是含有乙丙长序列链结构样品熔融慢冷结晶。     

聚丙烯与聚酯-聚醚多嵌段共聚物共混的研究

聚丙烯和聚酯-聚醚多嵌段共聚物的熔融共混物是微多相分散体系,其力学性能和软链段的结构有关。DSC和偏光显微镜图分别表明共混物中聚丙烯结晶度以及球晶尺寸随聚酯-聚醚的混入量而变小。聚丙烯和少量聚酯-聚醚多嵌段共聚物共混,可改进聚丙烯的流变性,吸湿性和染色性。     

聚（β－羟基丁酸酯）／聚双酚A羟基醚共混体系相容性及结构的研究

ＤＳＣ和ＦＴＩＲ测试表明，结晶／非晶共混体系聚（β－羟基丁酸酯）（ＰＨＢ）／聚双酚Ａ羧基醚是部分相容的。熔融结晶退火可以大大提高共混物的结晶度，增加其相容性。７５／２５组分ＰＨＢ相结晶度最大，５０／５０组分晶面微晶尺寸最大。     

Stability of the γ form and the development of the α form in nylon 6

The structure of nylon 6 fibers is analyzed by x-ray diffraction. Our results suggest that only two forms of nylon 6, α and γ, along with lattice distortion and crystallite size, are sufficient to explain the whole range of crystalline structures observed in nylon 6. The γ phase is the preferred initial form in a number of nylon 6 samples. The lattice distortion of the γ form along the chain axis varies from 0.8 to 2.4%, depending on the processing conditions. Upon annealing nylon 6 fibers, the α form is produced primarily by γ-to-α conversion in high-orientation fibers, while additional α form can also crystallize from the amorphous phase in low-orientation fibers. Finally, we show that α crystallites are favored during conditioning of poorly crystallized fibers in a humid atmosphere, and therefore fibers with α as the major crystalline form are produced upon drawing these conditioned fibers. Fibers drawn without lag time contain primarily the γ phase.     

尼龙-6和尼龙-6合金的球晶结构与破坏性能的研究

成型冷却速度即结晶速度对单纯尼龙 ６和尼龙 ６合金的拉伸破坏性能具有不同的影响．结晶速度慢，球晶尺寸大，单纯尼龙 ６的拉伸破坏强度高，破坏形变和破坏能量减小；尼龙 ６／热塑性聚酰胺弹性体／增容剂合金不仅拉伸破坏强度高，而且破坏形变和破坏能量都有所增加．研究表明，虽然球晶尺寸影响尼龙 ６的破坏性能，但球晶的性质即球晶的界面上和片晶 片晶间的非晶部分结构、微小分散粒子的空洞化及相与相之间的界面结合强度是影响尼龙 ６破坏性能的主要因素．     

熔体插层制备尼龙6/蒙脱土纳米复合材料的性能表征

通过熔体插层成功地制备了尼龙６／蒙脱土纳米复合材料，测试了力学性能、耐热性能和耐溶剂性．通过ＴＥＭ、ＷＡＸＤ、ＤＳＣ等手段，研究了结构与结晶行为，并与插层聚合的尼龙６／蒙脱土纳米复合材料进行了对比．实验表明通过熔体插层可使尼龙６基体插层于蒙脱土中，所得到的复合物的性能较尼龙６有很大提高，且与插层聚合的尼龙６／蒙脱土纳米复合材料的性能相当．     

STUDY ON THE BLENDS OF NYLON 66 AND LIQUID CRYSTALLINE POLYESTERS

Blends of polyamide (Nylon 66) with two different kinds of liquid crystalline polyesters were studied in all the composition range. Homogeneous samples were obtained by coprccipitation from 2 wt%. solution of blends. The thermal properties, crystallinity and morphology of these blends were studied by using DSC, polarizing microscopy, and scanning electron microscopy. The phase transition and morphology of the blends are markedly-influenced by the composition of liquid crystalline polyesters. The mechanical behaviour of PHB/HNA-Nylon 66 blend was improved. although polyamidc (Nylon 66)with the liquid crystalline polyesters were incompatible, but a rather strong interaction between the polymers did exist.     

Studies on crystalline forms of nylon 6. II. Crystallization from the melt

The relative amounts of the α and the γ crystalline forms of nylon 6 obtained from the melt under different crystallization conditions have been studied by an x-ray diffraction procedure by comparison with a calibration curve obtained from the diffraction of standard samples. The weight fraction of the α form decreases with increasing crystallization temperature and that of the γ form increases. Growth of the α form is predominant in crystallization at 100°C and of the α form at 200°C. The amount of the α form tends to increase on annealing at 200°C for specimens crystallized at any temperature.     

Structural and mechanical behavior of nylon 6 films part I. Identification and stability of the crystalline phases

The crystalline phase of polyamide 6 (otherwise nylon 6) films produced following various physical treatments is investigated by means of thermal analysis, X‐ray diffraction, and infrared spectroscopy. A recently published procedure for treating infrared spectra of multicomponent compounds without a priori knowledge of the individual component spectra allowed us to perform a semiquantitative analysis of the structural changes upon annealing, including data from drawn samples. Melt‐cast films display a mesomorphic state that is thermally stable up to about 120 °C. This structure partly reorganizes into the stable monoclinic α form above 120 °C. Films in major γ form produced by iodine treatment are thermally stable up to 200 °C. Films in major α form are also prepared by superheated water treatment. No evidence is given for a Brill transition about 170 °C. This is an important fact for further understanding of the drawing behavior of PA6 at temperatures above and below this domain. The mesomorphic phase can hardly be separated from the amorphous component both from X‐ray and infrared analysis. However, scanning calorimetry, which is often criticized due to possible reorganization of unstable species during the heating scan, turned out to be a very useful technique. Indeed, recrystallization from the amorphous phase or improvement of ordering from the mesomorphic state both result in exothermic effects in quite different temperature domains that allow to discriminate the two phenomena. © 2001 John Wiley & Sons, Inc. J Polym Sci B: Polym Phys 39: 484–495, 2001     

Relations between dynamic mechanical properties and melting behavior of nylon 66 and poly(ethylene terephthalate)

Nylon 66 films exhibiting form I melting behavior show the γ mechanical relaxation at ?140°C. Samples which have form II melting behavior do not show this relaxation. The γ relaxation disappears when material having form I behavior is converted to material having form II behavior by annealing or by cold drawing. The form I and form II types of melting behavior are also found in poly(ethylene terephthalate); the interconversions and thermal behavior of the forms are analogous to the nylon 66 case. In poly(ethylene terephthalate), the β relaxation at ?40 to ?60°C is present only when form I melting behavior is found. Conversion to form II melting behavior by annealing or drawing (80°C) again causes the relaxation to disappear. No β relaxation was found in amorphous polymer. The γ dispersion in nylon 66 and the β dispersion in poly(ethylene terephthalate) can therefore be associated with the crystalline structure responsible for form I melting behavior. Form I melting behavior has been associated with foldedchain crystals based on previous work. It is therefore postulated that the γ dispersion in nylon 66 and the β dispersion in poly(ethylene terephthalate) are associated with motions in the chain folds. This assignment is not inconsistent with the change in the γ dispersion of nylon 66 with the number of backbone CH₂ units, since these will affect the fold structure.     

MULTIPLE MELTING AND CRYSTALLIZATION BEHAVIOR OF NYLON 1212

The wide-angle X-ray diffraction (WAXD) patterns of isothermally crystallized Nylon 1212 show that γ-form crystals form below 90℃ and the α-form crystals can exist above 140℃. In the temperature range of 90-140℃, the α-form and γ-form crystals coexist. Variable-temperature WAXD exhibits that the nylon 1212 γ-form does not show crystal transition on heating, while α-form isothermally crystallized at 160℃ exhibits Brill transition at a little higher than 180℃ on heating. The multiple melting behaviors of Nylon 1212 isothermally crystallized from melt come from a complex mechanism of different crystal structures, dual lamellar population and melting-recrystallization. In polarized optical microscope (POM) observations, Nylon 1212 isothermally crystallized at 175℃ shows the ringed banded spherulites. However, at temperatures below 160℃ the ringed banded image disappears, and cross-extinct spherulites are formed.     

FTIR spectroscopic characterization of structural changes in polyamide‐6 fibers during annealing and drawing

First, we report the development of Fourier transform infrared (FTIR) spectroscopic methods to determine the α/γ‐crystalline phase ratio of polyamide‐6 fibers and, in combination with density measurements, the total crystallinity. Using density determinations of the crystallinity of pure α and pure γ samples, we found the absorption coefficient ratio for the 930 (α) and 973 cm⁻¹ (γ) bands to be 4.4, from which we could obtain the α/γ ratio for any polyamide‐6 sample. The application of this FTIR method to the quantitative analysis of phase changes during thermal treatment and the drawing of polyamide‐6 was then made. We confirmed that crystallization during thermal treatments involved increases in both phases and did not involve crystal‐to‐crystal transformation, whereas drawing involved both crystallization of the amorphous phase in the α form and γ→α transformation. Finally, we revisited the band assignments for the amorphous phase of polyamide‐6 and found that the band at 1170 cm⁻¹ was not an amorphous band but, because its absorbance was independent of crystallinity, could be used as an internal reference band. The band at 1124 cm⁻¹ was reliably attributed to the amorphous phase. © 2001 John Wiley & Sons, Inc. J Polym Sci B: Polym Phys 39: 536–547, 2001