Reinforced hydrogels for silicone copolymer delivery for scar remediation

Hypertrophic scars are formed by collagen overproduction in wounded areas and often occur in victims of severe burns. There are several methods for hypertrophic scar remediation and silicone gel therapy is one of the more successful methods. Research by others has shown that the activity of these gels may be due to migration of amphiphilic silicone oligomers from the gel and into the dermis, down-regulating production of collagen by fibroblasts. Normal silicone oil (PDMS) does not produce the same effect on fibroblasts. The main purpose of this project is the introduction of a particular amphiphilic silicone rake copolymer into an appropriate network which can absorb and release the silicone copolymer on the scarred area. Hydrogels are polymeric crosslinked networks which can swell in water or a drug solution, and gradually release the drug when applied to the skin. The application of gel enhances the effectiveness of the therapy, reduces the period of treatment and can be comfortable for patients to use. Polyethylene glycol (PEG) based networks have been applied in this research, because the amphiphilic silicone rake copolymer to be used as a therapy has polyethylene oxide (PEO) as a side chain. These PEO side chains have very similar chemical structure to a PEG gel chain so enhancing both the compatibility and the diffusion of the amphiphilic silicone rake copolymer into and out of the gel. Synthesis of PEG-based networks has been performed by two methods: in situ silsesquioxane formation as crosslink with a sol-gel reaction under different conditions and UV curing. PEG networks have low mechanical properties which is a fundamental limitation of the polymer backbone. For mechanical properties enhancement, composite networks were synthesized using nano-silica with different surface modification. The chemical structure of in situ silsesquioxane in the dry network has been examined by Solid State NMR, Differential Scanning Calorimetry (DSC) and swelling measurements in water. Mechanical properties of dry networks were tested by Dynamic Mechanical Thermal Analysis (DMTA) to determine modulus and interfacial interaction between silica and the network. In this way a family of self-reinforced networks has been produced that have been shown to absorb and deliver the active amphiphilic silicone- PEO rake copolymer.

Enzymatically degradable EMI shielding materials derived from PCL based nanocomposites

In this study, two different types of multiwall carbon nanotubes (MWNTs) namely pristine (p-MWNTs) and amine functionalized (a-MWNTs) were melt-mixed with polycaprolactone (PCL) to develop biodegradable electromagnetic interference (EMI) shielding materials. The bulk electrical conductivity of the nanocomposites was assessed using broadband dielectric spectroscopy and the structural properties were evaluated using dynamic mechanical thermal analysis (DMTA). Both the electrical conductivity and the structural properties improved after the addition of MWNTs and were observed to be proportional to the increasing fractions in the nanocomposites. The shielding effectiveness of the nanocomposites was studied using a vector network analyzer (VNA) in a broad range of frequencies, X-band (8 to 12 GHz) and K-u-band (12 to 18 GHz) on toroidal samples. The shielding effectiveness significantly improved on addition of MWNTs, more in the case of p-MWNTs than in a-MWNTs. For instance, at a given fraction of MWNTs (3 wt%), PCL with p-MWNTs and a-MWNTs showed a shielding effectiveness of -32 dB and -29 dB, respectively. Moreover, it was observed that reflection was the primary mechanism of shielding at lower fractions of MWNTs, while absorption dominated at higher fractions in the composites. As one of the rationales of this work was to develop biodegradable EMI shielding materials to address the challenges concerning electronic waste, the effect of different MWNTs on the biodegradability of PCL composites was assessed through enzymatic degradation. The enzymatic degradation of the samples cut from the hot pressed films by bacterial lipase was investigated. It was noted that a-MWNTs exhibited almost similar degradation rate as the control PCL sample; however, p-MWNTs showed a slower degradation rate. This study demonstrates the potential use of PCL-MWNT composites as flexible, light weight and eco-friendly EMI shielding materials.

Anomalous Thermal Stability of Nd-Fe-Co-Al Bulk Metallic Glass

The thermal stability of Nd60Fe20Co10Al10 bulk metallic glass (BMG) has been studied by differential scanning calorimetry (DSC), dynamic mechanical thermal analysis (DMTA), isochronal dilatation and compression tests. The results show that the glass transition of the BMG takes place quite gradually between about 460 and 650 K at a heating rate of 0.17 K/s. Several transformation processes are observed during continuous heating with the first crystallization process beginning at about 460 K, while massive crystallization takes place near the solidus temperature of the alloy. The positive heat of mixing between the two major constituents, Nd and Fe, and, consequently, a highly inhomogeneous composition of the attained amorphous phase are responsible for the anomalous thermal stability in this system. (C) 2002 Acta Materialia Inc. Published by Elsevier Science Ltd. All rights reserved.

Glass transition and crystallization process of hard magnetic bulk Nd60Al10Fe20Co10 metallic glass

Glass transition and crystallization process of bulk Nd60Al10Fe20Co10 metallic glass were investigated by means of dynamic mechanical thermal analysis (DMTA), differential scanning calorimetry (DSC), X-ray diffraction (XRD) and scanning electronic microscopy (SEM). It is shown that the glass transition and onset crystallization temperature determined by DMTA at a heating rate of 0.167 K/s are 480 and 588 K respectively. The crystallization process of the metallic glass is concluded as follows: amorphous alpha-->alpha' + metastable FeNdAl novel phase -->alpha' + primary delta phase-->primary delta phase + eutectic delta phase Nd3Al phase + Nd3Co phase. The appearance of hard magnetism in this alloy is ascribed to the presence of amorphous phase with highly relaxed structure. The hard magnetism disappeared after the eutectic crystallization of amorphous phase.

Nd65Al10Fe25-xCox (x=0,5,10) bulk metallic glasses with wide supercooled liquid regions

Bulk metallic glasses of Nd65Al10Fe25-xCox (x=0,5,10) have been prepared in the form of 3 mm diam rods. Results of differential scanning calrimetry, dynamic mechanical thermal analysis (DMTA), and x-ray diffraction are presented for these alloys. It is shown that the glass transition and crystallization have been observed by DMTA. The reduced glass transition temperature of these glasses, defined as the ratio between the glass transition temperature T-g and the melting temperature T-l is in the range from 0.55 to 0.62. All these glasses have a large supercooled liquid region (SLR), ranging from 80 to 130 K. The high value of reduced glass transition temperature and wide SLR agree with their good glass formation ability.

Glass Transition and Thermal Stability of Hard Magnetic Bulk NdAlFeCo Metallic Glass

Glass transition and thermal stability of bulk Nd60Al10Fe20Co10 metallic glass were investigated by means of dynamic mechanical thermal analysis (DMTA), differential scanning calorimetry (DSC), X-ray diffraction (XRD) and scanning electronic microscopy (SEM). The glass transition temperature, not revealed by DSC, is alternatively determined by DMTA via storage modulus E' and loss modulus E" measurement to be 498 K at a heating rate of 0.167 K s (-1). The calculated reduced glass transition temperature (T-g/T-m) is 0.63. The large value of T-g/T-m of this alloy is consistent with its good glass-forming ability. The crystallization process of the metallic glass is concluded as follows: amorphous --> amorphous + metastable FeNdAl phase --> amorphous + primary delta-FeNdAl phase --> primary delta-phase + eutectic delta-phase + Nd3Al + Nd3Co. The appearance of hard magnetism in this alloy is ascribed to the presence of amorphous phase with highly relaxed structure. The hard magnetism disappeared after the eutectic crystallization of the amorphous phase. (C) 2002 Elsevier Science B.V. All rights reserved.

由异构的二苯醚二酐和二苯硫醚二酐合成的聚酰亚胺

本论文的目的是研究由桥联二配的异构体合成的聚酰亚胺的性质，期望能发现既不牺牲热性能和机械性能又能改善加工性的新型聚酰亚胺材料。国内外目前在此方面的研究还较少，对异构化聚酰亚胺进行系统研究既填补了基础研究在此方面的空白，也对发展新的聚酰亚胺品种具有很天的实际意义。本论文在聚酞亚胺组过去工作的基础上，以氯代苯配为原料合成了二苯醚二配（ODPA）和二苯硫醚二酐（TDPA）两种桥联二配的3，3'-位和3，4'-位异构体（以桥键相对苯酐单元的位置命名），并得到了3，3’一ODPA和3，4'-ODPA的单晶，发现它们的顺反构象在单晶中都能稳定存在，其扭曲结构对聚合物的性质有很大影响。本论文还以三种ODPA异构体和三种TDPA异构体为基础合成了一系列的热塑性聚酰亚胺，对它们的性质进行了研究，发现以3，3'-位和3，4'-位二配为基础的聚酰亚胺在酚类溶剂和DMAc、DMF、NMP等极性溶剂中具有良好的溶解性，在DMSO和CHC13中部分溶解，而以4，4'-位二配为基础的聚酰亚胺则只溶于酚类溶剂。异构ODPA和TDPA系列基于同种二胺的聚酰亚胺薄膜都具有高的耐热性，后者的热氧化稳定性比前者稍高。以3，3'-位二酐为基础的聚酰胺酸热亚胺化的薄膜较脆，但由它们化学亚胺化后的聚酰亚胺粉末再溶解可得优良力学性能的韧膜。以3，4'-位二醉和4，4'-位二配为基础的聚酰胺酸热亚胺化薄膜具有相近的优异力学性质。对以4，4'-ODPA为主的共聚、共混聚酰胺酸热亚胺化薄膜力学性能的研究表明，当3，3'-OD队的含量超过30％时，薄膜脆性明显增加，而3，4'-ODPA以任何比例和4，4'-ODPA共聚、共混都能得到强韧的薄膜。异构TDPA系列聚酰亚胺的力学性能同ODPA系列相当。由异构ODPA和TDPA系列合成的聚酰亚胺动态力学性质规律相同。它们的玻璃化转变温度（Tg）均为3，3'-位的最高，3，4'-位次之，4，4'-位的最低。对于β转变，均为4，4'-位的Tβ最高，β转变峰也最强，3，4'-位的Tβ较低，β转变峰也稍弱，3，3'-位的β转变最弱，没有明显的β转变峰。由ODPA系列异构体同ODA共聚、共混的热酞亚胺化聚酰亚胺薄膜除3，3'-ODPA含量为75％时膜脆DMTA未测外，其他共聚、共混聚酰亚胺薄膜的Tg均随4，4'-位含量的增加而降低，Tp随4，4'-位含量的增加而升高，β转变峰的强度也随4，4'-位含量的增加而增大，Tp（K）/Tg（K）数值均在0.68～0.75之间。含3，3'-位和3，4'-位二配的聚酰亚胺薄膜在Tg过后不久即被迅速拉长至伸长率超过30％（DMTA仪器的设限），而由4，4'-位二酐合成的聚酰亚胺则到450℃伸长率均未超30％。经对ODPA系列异构体同·ODA聚合的聚酰亚胺薄膜拉伸前后的WAXD研究发现，4，4'-ODPA/ODA的薄膜在拉伸前后结晶峰无变化，表明Tg前后其分子间均有较大的作用力，其他两种膜拉伸后有明显的取向结晶现象，由此可见它们在Tg后的迅速伸长可能是因为其扭曲结构使得分子链堆积疏松，链段的活动性随自由体积的增大而迅速增强。对中等分子量的异构ODPA和TDPA系列同ODA聚合的聚酰亚胺的流变性质研究发现，3，4'-位聚酰亚胺拥有最低的熔体粘度，可能因为其分子堆积比4，4'-位的疏松，而链刚性又比3，3'-位的弱。由异构ODPA和TDPA系列与不同二胺和封端剂合成的PMR型热固性聚酰亚胺流变性质规律不尽相同。异构ODPA/MDA/NA的PMR树脂中3，3'-位树脂熔融粘度谷底数值较高加工窗口较窄。异构ODR入／ODA/NA的PMR树脂中三者熔融粘度谷底相同，均在SPa·s左右，3，3'-位和3，4'-位树脂的加工窗口几乎重合，4，4'-位树脂加工窗口随不同次制样的结晶性不同而有所变化。同异构ODPA/ODA/NA的PMR树脂相比，异构TDPA／ODA/NA系列的熔融粘度谷底数值稍高（10～14Pa·s之间），但也彼此相同，无异构体间的差别，3，4'-位和4，4，一位树脂加工窗口均较宽且4，4'-位树脂无明显结晶出现，3，3'-位窗日最窄。异构TDPA/ODA/PEPA的PMR树脂熔融粘度谷底比NA封端的低，降到2-4Pa·s左右，且加工窗口大大加宽，异构体之间差别不大，熔融粘度谷底数值比4，4'-ODPA/ODA/PEPA树脂低，窗口也宽。以3，4’-ODA取代4，4'-ODA后，由4，4'-TD队、3，4'-TD队、3，4'-ODPA和4，4’-OD队合成的PE以封端PMR树脂均拥有1 Pa·s左右的熔体粘度谷底。4，4'-ODPA／3，4'-ODA／PEPA结晶性较强，加工窗口在290℃以上，其他三种树脂的加工窗口都可扩宽到270～350℃，可望适合用RrM工艺加工高性能的复合材料。总体看来，异构ODPA和TDPA系歹lJ的PMR树脂中，由4，4'-ODPA合成的树脂有较强的结晶性，由3，3'-位二配合成的树脂熔体粘度和加工窗口多有变化，但由4，4'-TDPA和3，4'-位二酐合成的不同种类树脂和其异构体相比均具有较低的熔体粘度谷底和较宽的加工窗口，可见异构TDPA系列的热固性聚酰亚胺熔融加工性比异构ODPA系列好。

含侧链苯炔基的热固性聚酰亚胺薄膜

采用3,3,′4,4′-联苯四酸二酐(3,3,′4,4-′BPDA)和3种二胺,3,5-二氨基-4′-苯炔基二苯甲酮(DPEB)、4,4′-二氨基二苯醚(4,4-′ODA)及4,4′-二氨基二苯甲酮(4,4-′DABP),以苯酐(PA)为封端剂制备了不同比例的带苯炔侧基的聚酰亚胺薄膜,采用DMTA、TGA和力学性能测试等分析技术对侧链含苯乙炔基的聚酰亚胺膜的性能进行了表征。

Polyimides Derived from 1,4-Bis [3-oxy-(N-aminophthalimide)] Benzene

A novel diamine, 1,4-bis [3-oxy-(N-aminophthalimide)] benzene (BOAPIB), was synthesized from 1,4-bis [3-oxy-(N-phenylphthalimide)] benzene and hydrazine. Its structure was determined via IR, H-1 NMR, and elemental analysis. A series of five-member ring, hydrazine-based polyimides were prepared from this diamine and various aromatic dianhydrides via one-step polycondensation in p-chlorophenol. The inherent viscosities of these polyimides were in the range of 0.17-0.61 dL/g. These polymers were soluble in polar aprotic solvents and phenols at room temperature. Thermogravimetric analysis (TGA) showed that the 5% weight-loss temperatures of the polyimides were near 450 degrees C in air and 500 degrees C in nitrogen. Dynamic mechanical thermal analysis (DMTA) indicated that the glass-transition temperatures (T(g)s) of these polymers were in the range of 265-360 degrees C. The wide-angle X-ray diffraction showed that all the polyimides were amorphous.

Studies on syntheses and properties of novel CeO2/Polyimide nanocomposite films from Ce(Phen)(3) complex

A series of cerium dioxide (CeO2,)/polyimide (PI) nanocomposites were successfully prepared from Ce(Phen)(3) and polyamic acid (PAA) via the solution direct-dispersing method, followed by a step thermal imidization process. TGA and XPS studies showed that the cerium complex decomposed to form CeO2, during the thermal imidization process at 300 degrees C. SEM observation showed that the formed CeO2, as nalloparticles was well dispersed in polyimide matrix with a size of about 50-100 nm for samples with different contents of CeO2. Thermal analysis indicated that the introduction of CeO2, decreased the thermal stability of nanocomposite films due to the decomposition of Ce(Phen)(3) in the imidization process, while the glass transition temperature (T-g) increased obviously. especially nanocomposite films with high loading of CeO2 exhibited a trend of disappearance off, DMTA and static tensile measurements showed that the storage modulus of nanocomposite films increased, while the elongation at break decreased with increasing CeO2 content.

Polyimides derived from 3,3 '-bis(N-aminophthalimide)

A novel diamine, 3,3'-bis(N-aminophthalimide) (BAPI), was prepared from 3,3'-bis(N-phenylphthalimide). Its structure was determined via IR, H-1 NMR, N-15 NMR, elemental analysis, and single-crystal X-ray diffraction analysis. A series of homo- and copolyimides were synthesized by a conventional one-step method in p-chlorophenol. The characteristic IR absorption bands of hydrazine-based imide groups were near 1780, 1750, 1350, 1100, and 730 cm(-1). The polymers showed good solubility in polar aprotic solvents and phenols at room temperature. The temperatures of 5% weight loss (T-5%) of the polyimides ranged from 495 to 530 degrees C in air. DMTA analyses indicated that the glass-transition temperatures (Tgs) of the polyimides were in the range 371-432 degrees C. These polymers had cutoff wavelengths between 350 and 400 nm. The polyimide films of 6FDA/BAPI and 4,4'-HQPDA/BAPI were colorless; other films were pale yellow or yellow.

Polystyrene and asphaltene micelles within blends with a bitumen of an SBS block copolymer and styrene and butadiene homopolymers

Using fluorescence microscopy, DSC and DMTA we have explored blends of a bitumen with a styrene-butadiene-styrene (SBS) block copolymer, and with blends of the bitumen with SBS and one or two homopolymers - a polystyrene and a poly(cis-butadiene). The SBS polymer was progressively replaced with quantities of the homopolymers both together in the proportions found in the block copolymer and then by each homopolymer separately. At low temperatures the blends are all softer than the bitumen itself, so the polymers plasticise the bitumen-rich phase, and above 50°C the blends' stiffness (E') falls below a plateau only when a critical proportion of the block copolymer has been replaced with the two homopolymers: this supports the idea of an extensive network created by the polystyrene-rich spherical microphases that is effective even when the polystyrene microphases have melted. In one polymer blend the stiffness rose as the temperature was raised above 100°C, suggesting the development of a mesophase based upon polybutadiene plus asphaltenes, in another E' was enhanced and E" remained constant as the temperature rose above 70°C, perhaps for a similar reason; in some loss process appeared and the stiffness fell as temperature rose; but in others a good part of the SBS was replaced by either polystyrene or polybutadiene without changing the appearance of a rubbery plateau, that is, without a diminution of the mechanical properties of the soft matter.

Structure-Property Relationships in Biaxially Deformed Polypropylene Nanocomposites

Semi-solid forming processes such as thermoforming and injection blow moulding are used to make much of today’s packaging. As for most packaging there is a drive to reduce product weight and improve properties such as barrier performance. Polymer nanocomposites offer the possibility of increased modulus
(and hence potential product light weighting) as well as improved barrier properties and are the subject of much research attention. In this particular study, polypropylene–clay nanocomposite sheets produced via biaxial deformation are investigated and the structure of the nanocomposites is quantitatively determined in order to gain a better understanding of the influence of the composite structure on mechanical properties. Compression moulded sheets of polypropylene and polypropylene/Cloisite 15A nanocomposite (5 wt.%) were biaxially stretched to different stretching ratios, and then the structure of
the nanocomposite was examined using XRD and TEM techniques. Different stretching ratios produced different degrees of exfoliation and orientation of the clay tactoids. The sheet properties were then investigated using DSC, DMTA, and tensile tests .It was found that regardless of the degree of exfoliation or
orientation, the addition of clay has no effect on percentage crystallinity or melting temperature, but it has an effect on the crystallization temperature and on the crystal size distribution. DMTA and tensile tests show that both the degree of exfoliation and the degree of orientation positively correlate with the dynamic mechanical properties and the tensile properties of the sheet.

Pharmaceutical applications of dynamic mechanical thermal analysis

The successful development of polymeric drug delivery and biomedical devices requires a comprehensive understanding of the viscoleastic properties of polymers as these have been shown to directly affect clinical efficacy. Dynamic mechanical thermal analysis (DMTA) is an accessible and versatile analytical technique in which an oscillating stress or strain is applied to a sample as a function of oscillatory frequency and temperature. Through cyclic application of a non-destructive stress or strain, a comprehensive understanding of the viscoelastic properties of polymers may be obtained. In this review, we provide a concise overview of the theory of DMTA and the basic instrumental/operating principles. Moreover, the application of DMTA for the characterization of solid pharmaceutical and biomedical systems has been discussed in detail. In particular we have described the potential of DMTA to measure and understand relaxation transitions and miscibility in binary and higher-order systems and describe the more recent applications of the technique for this purpose. © 2011 Elsevier B.V.