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Segmented Copoly(Ether-Ester) Elastomers

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Segmented Copoly(Ether-Ester) Elastomers Polymer Journal, Vol. 26, No. 7, pp 804-815 (1994) Segmented Copoly(ether-ester) Elastomers. Influence of Hard Segment Length and Substitution on Mesophase Formationt M. M. S0NPATKI, K. RAVINDRANATH,tt and S. PONRATHNAM* Chemical Engineering Division, National Chemical Laboratory, Pune-411008, India (Received September 24, 1993) ABSTRACT: Syntheses of segmented copoly(ether-ester)s with (oxy-1,4-phenyleneoxycarbonyl­ l,4-phenylenecarbonyl)/( oxy-2-methyl-1,4-phenyleneoxycarbonyl- I ,4-phenylenecarbonyl) (methyl series)/( oxy-2-chloro-1,4-phenyleneoxycarbonyl-l ,4-phenylenecarbonyl) (chloro series) hard seg­ ments and poly(oxytetramethylene) soft segments, are reported. The methodology consisted of sequential melt condensation of terephthaloyl chloride with poly(oxytetramethylene)glycol (M. = 250) [POTMG] and hydroquinone (HQ)/methylhydroquinone (Me-HQ)/chlorohydroquinone (Cl-HQ). Hard segment length as well as substitution in core of hard segment were varied (H to CH3 /Cl) while maintaining the soft segment length constant. Copolymers were characterised for solubility behavior and by infrared spectroscopy, X-ray diffraction, DSC and polarising microscopy. Thermal properties were found to be dependent on average length of hard segment as well as on the type of substituent in the core of hard segment. All copoly( ether-ester)s are elastomeric at room temperature (25°C). Some of the polymers synthesised exhibit thermotropic liquid crystalline behavior. KEY WORDS Segmented Copoly(ether-ester)s / Hard Segment / Soft Segment/ Random Copolymers/ Thermotropic Liquid Crystalline Polymers / Mesophase / Thermotropic Elastomers / Thermal Properties / Segmented thermoplastic elastomers1 based (amorphous systems) or melting temperature, on copolyether-esters2 •3 are well known. The Tm (crystalline systems) of hard segments. This physical characteristics are similar to cured high melt viscosity can be depressed by elastomers while processing is akin to those incorporating hard blocks exhibiting thermo­ used with rigid, glassy, or crystalline thermo­ tropicity, 4 which tend to form microscopic plastics. The soft blocks in such thermoplastic domains with a preferential order. One could copolymers, with alternating hard and soft also visualize unusual rheological and crystalli­ blocks, impart elastomeric aptitude above its sation characteristics originating from the glass transition temperature, Tgs while rigid rubber like elasticity coupled with directional blocks are responsible for the mechanical character of the mesogen. The liquid crystallin­ properties by providing physical crosslinks and ity will also influence molecular orientation reinforcement sites at this temperature. How­ after processing and finally the physical ever, incompatibility between soft and hard properties. A number of side chain liquid blocks generates a high melt viscosity while crystalline elastomeric systems have been 5 8 processing above the glass transition, T8h synthesised. - While work on main chain t NCL Communication No. 5872. tt Present address: Department of Chemical Engineering, University of Wisconsin, Madison, WI 53706, U.S.A. * To whom correspondence should be addressed. 804 Segmented Copoly(ether-ester) Elastomers systems have been in progress for some time, recrystallised using toluene whereas Cl-HQ was it is only very recently that Tsai9 reported such recrystallised from chloroform. Terephthaloyl a system with (alkylene 4,4'-bibenzoate) as chloride (TPC) was synthesised from TA and mesogenic hard segment. thionyl chloride in petroleum ether and Here we present syntheses and properties catalytic amount of dimethyl formamide. All of a new series of main chain thermoplastic apparatus were flame dried prior to use. elastomers wherein ( oxy-l ,4-phenyleneoxycar­ bonyl-1,4-phenylenecarbonyl)/(oxy-2-methyl- POLYMER SYNTHESIS 1,4-phenyleneoxycar bony1-1,4-pheny lene­ carbonyl) (methyl series) or ( oxy-2-chloro-1,4- Freshly recrystallised TPC was reacted with phenyleneoxycarbonyl- l ,4-phenylenecarbon­ POTMG (M. = 250) by slowly raising the yl) (chloro series) moieties act as hard segment reaction temperature from room temperature and poly(oxytetramethylene) act as soft seg­ to 90°C over a period of three hours under dry ment. The thermal properties of these copoly­ and pure nitrogen atmosphere with stirring to (ether-ester)s are presented and examined form oligo ether-ester with acid chloride end relative to structural variables. The effect of groups. Hydrogen chloride (side product) lib­ change in hard segment length as well as erated was scrubbed through aqueous alkali influence of substituent in the core of hard traps. Then HQ or Me-HQ or Cl-HQ was segment on the onset of thermotropicity are added to the reaction mixture containing oligo also discussed. ether-ester and unreacted terephthaloyl chlo­ ride and temperature of the reaction mixture EXPERIMENTAL was raised gradually to 200°C over three hours under dry, pure nitrogen blanket with stirring Terephthalic acid (TA), hydroquinone (HQ), and maintained at this temperature for a period methylhydroquinone (Me-HQ), chlorohydro­ of 30 minutes. Polymer obtained was purified quinone (Cl-HQ) and poly(oxytetramethylene) by extraction with petroleum ether, washed glycol (M.=250) (POTMG) were obtained sequentially with 5 wt¾ aqueous sodium bi­ from Aldrich Chemical Co. Inc., U.S.A. carbonate, water, methanol, and dried to con­ POTMG was dried overnight using activated stant weight. The mole ratio ofTPC/POTMG/ 4 A and 3 A molecular sieves. HQ was HQ was varied and substituent in the meso­ recrystallised using hot water. Me-HQ was genic core was changed from H to CH3 /Cl as Table I. Synthesis and soft segment thermal data of copoly(ether-ester)s obtained from terephthaloyl chloride, poly(oxytetramethylene)glycol 250 and hydroquinone LICp, Crystallinityd Sample code Composition• I,, lb/dig-I T,, in °C in% Jmo1- 1 K- 1 TBIH50 1: 0.5 :0.5 0.08 -27.8 77.54 19.9 TBIH67 1 : 0.33 : 0.67 0.10 -25.5 160.37 34.9 TBIH75 I: 0.25: 0.75 C -49.5 231.16 44.4 TBIH80 1 : 0.20: 0.80 C -48.2 104.60 48.9 TBIH83 I: 0.17: 0.83 C -48.2 87.12 50.9 • Molar ratio of terephthaloyl chloride: poly(oxytetramethylene)glycol 250: hydroquinone. h Intrinsic viscosity determined in 4-chlorophenol at 50°C. 0 Polymer insoluble in 4-chlorophenol. d Calculated from room temperature X-ray diffraction. Polym. J., Vol. 26, No. 7, 1994 805 M. M. SONPATKI, K. RAVINDRANATH, and S. PONRATHNAM shown in Tables I and III. differing structural moieties are ideally suited to study the structural effects on properties. POLYMER CHARACTERIZATION Such polymers with interesting property profiles are main chain thermotropic liquid The intrinsic viscosity, [17], of methyl crystalline polyesters. A variety of strategies substituted polymer solutions in 4-chloro­ have been established for the synthesis through phenol at 5O°C was measured using an Ub­ low temperature solution polycondensation. belohde viscometer. Infrared spectral mea­ Thus, nonmesogenic spacer is reacted either surements were made using potassium bro­ with (i) the mesogen having predetermined mide (KBr) discs with a Shimadzu IR-47O sequence resulting in sequentially ordered and Perkin-Elmer 1600 series FT-IR spectro­ copolymers10 or (ii) via staged addition photometer. X-Ray diffraction measurements technique without isolation/purification of were carried out using Philips PW 1730 X­ mesogen so as to form sequentially random ray diffractometer with CuKa target and nick­ copolymers with alternating spacer and meso­ el filter. Percent crystallinity was calculated by genic groups. 11 Reaction at high temperature measuring the relative areas under the leads to randomisation of comonomer se­ amorphous halo and crystalline peaks obtained quence.12 The use of a oligomeric spacer with from X-ray diffraction scan and taking a rntio a distribution of lengths between the two of the area under the crystalline peaks to the functional groups, instead of a specific well total area [amorphous+ crystalline]. Differ­ defined one, results in lower melting polymers. ential scanning calorimetric analysis were This is ascribable to a break in the structural conducted using Mettler-4OOO thermal analyser periodicity which disrupt packing efliciency. 13 and DSC-3O cell. Temperature calibration was In sequentially ordered polymers thermal made by using Indium-Lead-Zinc standard transitions occur at higher temperatures as and that of heat flow by using Indium standard. compared to their random counterparts.12 It All thermal analyses were run at a rate of has also been well established that substituting lO°Cmin-1 under dry nitrogen. The sample hydrogen in the mesogenic core with bulkier mass were between 5 to 7 mg. Samples were groups/units may result in melt processable analysed within two temperature ranges: liquid crystalline polymers due to disruption in between - 75 to 5O°C for soft segment glass lateral packing. 14 In random rigid rod flexible transition temperature and between 50 to spacer type main chain copolymers thermo­ 35O°C for hard segment transitions. Glass tropic character has been observed at high transition temperatures were taken at the dilutions of mesogens. 15·16 temperature of half devetrification. Second This concept can be extended to form heating and second cooling runs were also segmented thermotropic liquid crystalline recorded after heating the samples above the copoly(ether-ester) elastomers. We have syn­ first heating melting transition. Polarising thesised random segmented copoly(ether-ester) microscopic
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