聚丁二酸二乙酯(PES)、聚丁二酸二丙酯(PTS)及不同組成的共聚酯(PETSAs)，可藉由使用四異丙基鈦為觸媒，以直接聚縮和反應合成；由本質粘度與凝膠滲透層析儀(GPC)所得到的結果證明這個方法可成功合成出具有高分子量的聚酯。共聚酯的組成與鏈段分佈可由核磁共振儀(NMR)氫譜與碳譜得到，丁二酸二乙酯(ES)與丁二酸二丙酯(TS)單元的鏈段分佈發現乃是屬於無規的分佈。熱性質乃使用微差式掃瞄熱卡計(DSC)與熱重分析儀(TGA)來測量，所有的共聚酯皆僅得到一個玻璃轉移溫度(Tg)，在熱穩定性上也沒有明顯的差異產生。在本研究中嘗試使用偏光顯微鏡(PLM)來測量熱穩定性的方法，在不同的溫度預熔融後，觀察聚酯的等溫球晶成長速率，將速率暴增時的溫度定義為該聚酯的熱裂解溫度(Td)；PES與PETSA 95/05的熱裂解溫度為213 C與200 C，比TGA所得的結果低了約35-45 C。
聚酯在低於熔點5-10 C下等溫結晶所得的試片，以X射線繞射儀觀察可以發現在PES含量較多的共聚酯中，僅觀察到PES的晶型，共聚酯中TS單元部分可能排除於結晶之外而位於無規的部分；由X射線繞射儀的結果觀之，隨著TS成分的加入，PES共聚酯的結晶有明顯被抑制的現象產生。對於具可塑性的聚酯使用流變儀進行動態機械性質的測量，隨著TS成分的增加，聚酯的儲存模量有下降的現象，而在Tg以上，可以發現結晶度對儲存模量的影響。
在本研究中也利用等溫與非等溫結晶兩種方法，藉由偏光顯微鏡(PLM)來觀察可結晶聚酯的球晶成長速率，球晶成長速率會隨著TS成分的上升而下降。PES的regime II -III轉移溫度，約發生在71 C，與文獻值非常接近。PETSA 95/05與PETS 80/20的轉移溫度，則分別發生於65.0 C與51.4 C。由非等溫實驗所得的球晶成長速率在此與等溫實驗的結果進行比較，彼此間十分吻合，而由非等溫實驗所得的regime分析結果，也與等溫所得的數據相近。
球晶最大成長速率可藉由Okui所提出的Arrhenius與WLF表示法來表示球晶成長速率公式中的分子傳輸項，由PES的非等溫連續成長速率資料可以建構出PES晶體成長速率的主要曲線，並可由此畫出PES與PES含量較多的共聚酯球晶成長的通用曲線。而聚酯的側向表面自由能、撓曲表面自由能與鏈撓曲所需的功，在本研究中也進行計算。鏈撓曲所需的功會隨著TS成分的上升而逐漸下降。

Poly(ethylene succinate) (PES), poly(trimethylene succinate) (PTS) and their copolyesters with various compositions were synthesized through a direct polycondensation reaction with titanium tetraisopropoxide used as the catalyst. Results obtained from intrinsic viscosity and gel permeation chromatography (GPC) studies have significantly contributed to the preparation of polyesters with high molecular weight. Compositions and sequence distributions of the synthesized copolyesters were determined by analyzing the spectra of 1H NMR and 13C NMR. According to those results, the sequence distributions of ethylene succinate (ES) units and trimethylene succinate (TS) units were found to be random. Thermal properties were then characterized using differential scanning calorimeter (DSC) and thermogravimetric analyzer (TGA). All copolymers exhibited a single glass transition temperature (Tg). These polyesters did not significantly differ in thermal stability. Next, thermal stability was estimated using polarized light microscopy (PLM). Isothermal growth rates for polyesters were observed after pre-melting at various temperatures. The thermal degradation temperature (Td) was estimated, at which the growth rate for polyesters increased abruptly. The Td value of PES and PETSA 95/05 was found to be 213 and 200 °C, respectively, which was 35−45 °C lower than that determined by TGA.
Wide-angle X-ray diffractograms (WAXDs) were obtained for polyesters that were crystallized isothermally at a temperature 5−10 °C below their melting temperatures. Only the crystal form of PES was appeared in the diffractograms of PES-rich copolyesters. The TS units in polyesters may be excluded and located in the amorphous part of polyesters. WAXD results indicate that incorporating TS units into PES could significantly inhibit the crystallization behavior of the latter. Additionally, dynamic mechanical properties of moldable polyesters were investigated using a Rheometer operated at 1 Hz. Below Tg, incorporating TS units into PES led to a decline in the storage modulus, while above Tg, the effect of crystallinity on the storage modulus could be found.
The sphreulite growth rates for crystallizable polyesters were measured by PLM. The growth rate of polyesters decreased with an increasing moiety of TS units. The regime II→III transition of PES was estimated to occur at ca. 71 °C, which is extremely close to values in the literature. The regime transition of PETSA95/05 and PETSA 80/20 was found to be 65.0 °C and 51.4 °C, respectively. A dynamic crystallization experiment was performed by PLM and compared with time consuming isothermal experiments. Above data closely corresponded to those data points determined in the isothermal experiments. Results of the regime analysis for the continuous data of polyesters closely resembled those of isothermal experiments.
The maximum growth rate was formulated in Arrhenius and WLF expressions for the molecular transport term. A master curve of the crystal growth rate for PES was constructed based on the continuous data of PES. Plotting the reduced growth rates after normalization against the reduced temperatures revealed a universal master curve for PES and two PES-rich copolyesters. Finally, the lateral surface free energy, fold surface free energy and work for chain folding of polyesters were evaluated based on kinetic analysis. According to those results, the works for chain folding decreased with an increasing moiety of TS units.

Contents…………….………………………………………………………………….I
List of Schemes..……………………………………………………….…………….III
List of Tables..……………………………...…………………………………….......IV
List of Figures…..……………………..…………………………………………......VI
Abstract (Chinese)……………………………………………………………………X
Abstract……………………………………………………………………….……XII
Chapter 1
Introduction……………………………..……………………………....…1
1.1 Background…...……………….……………………………………..........1
1.2 Purposes of this study…..……………………….…………….....………5
Chapter 2
Literature review………………………………………………………......6
2.1 Synthesis of polyesters…………………………..……………..……...…6
2.2 Crystal structures…….………………………………………..………...…7
2.3 Spherulite growth rates ……………………………………………………8
2.4 Regime transition analysis.... ….…...…………………………………..11
2.5 Relationships for crystal growth rate to temperature…………………….13
2.6 Evaluation of works for chain folding……...……………….………… 15
2.7 Copolyesters……………………………………………………………16
2.7.1 Fox equation……………………………………………………..18
2.7.2 Johnson equation…………………………………………………..18
Chapter 3
Experimental………………………………..……………………………20
3.1 Materials…..………………………………………………………….…20
3.2 Synthesis………..………………………………………………….……20
3.3 Characterization..………………………...……………………………….21
3.3.1 Measurements of molecular weights ..………………………..…21
3.3.2 Measurements of intrinsic viscosity..….………………………..…21
3.3.3 Analyses of chemical micorstructures…………….……………….21
3.3.4 Measurements of melting temperature (Tm) and glass transition temperature (Tg)………...…………………………………………22
3.3.4.1 Preparation of specimens………………………………...22
3.3.4.2 Measurements of Tm…………………………………......22
I
3.3.4.3 Measurements of Tg……………………………………..23
3.3.5 Thermal stability…………………………………………………...23
3.3.5.1 Measurements by thermogravimetric analyzer (TGA)..….23
3.3.5.2 Analysis by polarized light microscope (PLM)…...………23
3.3.6 Wide-angle X-ray diffraction……………………………………23
3.3.7 Dynamic mechanical analysis………..……………………………24
3.4 Morphology andmeasurements of growth rates…………………….....…24
3.4.1 Isothermal method…………………………………………………24
3.4.2 Non-isothermal method…………………………………………....25
Chapter 4
Results and discussion………………………………………………..……26
4.1 Modifications for synthesis………………………..……………………..26
4.2 Intrinsic viscosity and molecular weights………………..………....……27
4.3 Compositions and sequence distribution…………...….…..……………..28
4.4 Thermal properties………..………………………….……..………….…30
4.4.1 Melting temperature (Tm)………………………….…...………...30
4.4.2 Glass transition temperature (Tg)………….……………………..31
4.5. Thermal stability………………………………………………………...32
4.5.1 TGA results……...……...………………………………………….32
4.5.2 PLM studies……..….………………………………………...……33
4.6 Crystal patterns...……………………….………………………………34
4.7 Dynamic mechanical properties..……..………….……………………35
4.8 Spherulite growth rate…………………………………………………....36
4.8.1 Growth rate determined from isothermal method………………....36
4.8.2 Growth rates determined from non-isothermal method…………...37
4.9 Regime transition analysis………………………………………………41
4.9.1 Isothermal results…………………………………………………41
4.9.2 Non-isothermal results……………………………………………..42
4.10 Master and universal curves…………………..……………………….43
4.11 Works for chain folding..……………..………………………………...45
Chapter 5
Conclusions…………………........................................................…........49
References…………....................................................................................................51
Publications……………………………………………………………………….114

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