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Volume 22, Issue 6
Displaying 1-8 of 8 articles from this issue
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V. EFFECTS OF AFTER HEAT-STRETCHING AND HEAT-RELAXING ON ULTIMATE TENSILE PROPERTIESAkira Takaku, Naoyuki Kishi1966 Volume 22 Issue 6 Pages 243-248
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSThe ultimate tensile properties for an after-heat stretched and a heat-relaxed fiber of acrylonitrile-methylacrylate copolymer have been measured under a condition of constant load and the results obtained are summarized as follows:
(1) The tensile strength and the ultimate elongation vary with the after-treatments, but the shape of the composite curve of the logarithmic tensile strength plotted against the logarithmic time to break is unchanged and independent of the after-treatments. Therefore it may be assumed that the after-treatments have no effects on a critical condition for rupture. The temperature dependence of the shift factor along the axis of the time to break can be also assumed to be independent of the after-treatments.
(2) From the previous result that the location on the logarithmic axis of the time to break for the composite curve of the tensile strength is linearly related to the reciprocal of a characteristic temperature Tc, it is deduced that Tc for the heat-relaxed fiber is nearly the same as the value for the untreated and that of Tc for the heat-stretched fiber is lower than that of the untreated.
(3) Assuming that the shift factor along the logarithmic axis of the ultimate elongation represents a relative concentration of active chain, the free energy difference ΔF_??_ between active and inactive chains is calculated. From the maximum values of ΔF_??_ it is concluded that the active chains in the heat-stretched fiber are in restricted state and those of the heat-relaxed fiber are in relaxed and stable state.
(4) The effective stretch ratios for the untreated and the heat-relaxed fibers calculated from the maximum value of the ultimate elongation (εb)max coinside with those values calculated from the shrinkage in a I2-KI aqueous solution of high I2 concentration, and for the after-heat stretched fiber the value calculated from (εb)max coinsides with that obtained in a low I2 concentration ofthe solution, The tensile strength of the after-stretched fiber depends on a lower order region of the fiber structure, and this consideration associates with the decrease in Tc observed for the after-heat stretched fiber.View full abstractDownload PDF (391K) -
Kenji Kamide1966 Volume 22 Issue 6 Pages 249-254
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSThermal stress arising in the polypropylene filament preventing its thermal-shrinkage was measured to study the micro-fine structural character of filament and the stabilizability of the dimension of fiber by thermo-setting.
Four kinds of polypropylene filament ranging in molecular weight from 5.81×104 to 2.51×105 were prepared under the same spinning and stretching conditions except the spinning temperature.
By analyzing thermal stress, fs, defined as force per unit cross-section of sample at room temperature, the following experimental results were obtained;
(1) when the rate of changing temperature is less than 1°C/min., fs -temperature relations is not affected by the rate of changing temperature.
(2) Thermal stress is observed only for stretched filaments not subjected to heat-treatment.
(3) Generally, thermal stress increases with temperature above 65_??_72°C, independently of molecular weight and of the stretching conditions.
(4) (fs)max, maximum value of fs, increases with stretching ratio, (fs)max of filament, prepared under the same stretching conditions, was found to be proportional to molecular weight.
(5) fs on filament which was thermostatted at the fixed lower temperature than that at (fs)max slighthy increases with time, on the rther hand, fs above that the temperature was constant within the limits of experimental precision.
(6) Thermal stress was completely changed reversibly below the temperature, to which filament is preliminary heated.
It is evident from the above results that the internal strain, given in the stretching process, must be responsible to thermal stress. The degree of release of the internal strain may depend on the nature of intermolecular interaction, in other words, on the nature of the states of aggregation, depending on temperature. It should be remarked that thermal stress can not be interpreted immediately with the orientation of polymeric chains. Futhermore, the qualitative concept of thermal stress is discussed in some details on the basis of the molecular theory.View full abstractDownload PDF (459K) -
(2). X-RAY DIFFRACTION DIAGRAM OF QUENCHED CRYSTAL OF ISOTACTIC POLYPROPYLENE (PSEUDO-HEXAGONAL) AND ITS ORIENTATION EVALUATIONHirokazu Takahara, Hiromichi Kawai1966 Volume 22 Issue 6 Pages 255-262
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSX-Ray diffration diagram of the quenched isotactic polypropylene is much affected by the quenching condition from the melt. When the quenching condition is mild, four sets of diffraction ring located at about 15. 3, 21. 3, 28. 5 and 42.7° (2θ) are usually observed. From the fiber diagram, indices of the four diffraction planes should be (hk 0), (hk 1), (hk 2) and (003), respectively. On the other hand, two of the four sets of diffraction ring at higher Bragg angle tend to disappear when the quenching condition become severe, and it may be assumed that the X-ray diffraction diagram of completely quenched polymer has to have only two sets of diffraction ring at about 15.3 and 21.3°.
Assuming that the quenched isotactic polypropylene crystal be hexagonal in either case(consiting of four or two sets of diffraction ring), the following results on the uniaxial orientation factor of crystal c-axis, crystal lattice spacing, and reciprocal lattice coordinate are obtained in contradiction to each other: in the latter case, the orientation factor obtained from X-ray diffraction of (hk 0) plane agrees quite well with that from infrared dichroic ratio, but there remains a considerable discrepance of the orientation factor obtined from (hk 0) from that of (hk 1) planes;in the former case, the observed lattice spacing of (hk 1) and (hk 2) planes fairly well with the calculated ones, but there are some difference of the lattice spacsng of (hk 0) plane and the reciprocal lattice coordinates between the observed and calculated values.
The orintation factor of crystal c-axis, however, can be evaluated from x-ray diffraction of (hk 0) plane assuming that the quenched crystal is hexagonal, and the unaxial orientation factor of the c-axis may be expressed by;
fE=-2feq.
where fE and feq are orientation factors of the crystal c-axis and of the reciprocal lattice vector of (hk 0) plane.View full abstractDownload PDF (528K) -
PLASTIC RUPTURE ACCMOPANIED BY DEFORMATION BANDMasataka Kurokawa, Takashi Konishi, Moto Sakano1966 Volume 22 Issue 6 Pages 263-268
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSA deformation band is observed when a drawn polyethylene film is redrawn in the direction with an inclined angle to the original drawn direction, Usually the deformation band is not formed clearly in unannealed samples, but if the original drawn film is notched properly before redrawing, the band is formed clearly. When the notched sample is redrawn, rupture starts from the top of notch and proceeds in a direction inclined to the fibre axis of the original drawe film. Following with this rupture process, the deformation band is formed. The angle between the direction of original drawing and that of proceeding of the rupture was measured to study of the nature of these deformation band. This angle is not constant, but decreases with increasing degree of orientation and of crystallinity of orginal drawn film. The value of birefringence within a deformation band shows that molecules in it are highly oriented independently of the extension of original drawn film. From these results it is concluded that the bands do not represent twin deformation but a deformation similar to that involved in necking phenomenon,View full abstractDownload PDF (2388K) -
(IX). N-(2-CHLOROETHYL) SULFONAMIDES OF STYRENE-MALEIC ACID AND STYRENE-ITACONIC ACID COPOLYMERSSeishi Machida, Mutsushi Sakai, Gendo Nishitani1966 Volume 22 Issue 6 Pages 269-273
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSStyrene-maleic acid and styrene-itaconic acid copolymers were chlorosulfonated and subsequently reacted with 2-chloroethylamine to give N-(2-chloroethyl) sulfonamides of these copolymers.
Products containing about 0.5 of N-(2-chloroethyl) sulfonamide group per phenyl group were obtained. The derivatives are soluble in alkali to give viscous solutions.
Cotton fabrics treated with the alkaline solution of the derivative were found to increase in weight by 6_??_10 percent, and the polymer attached to the fibers was not shed by the ordinary soaping. It is considered that the polymer combines chemically with the fibers.
The N-(2-chloroethyl) sulfonamides of the polymers may be utilized as reactive paste and adhesive.View full abstractDownload PDF (387K) -
(5) EFFECT OF K2Cr2O7-OXYCELLULOSE ON PAPER MAKING (6) EFFECT OF NaClO-OXYCELLULOSE ON PAPER MAKINGShiro Takahashi1966 Volume 22 Issue 6 Pages 274-284
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSDownload PDF (815K) -
STUDY ON THE MANUFACTURING OF THE COMPOUND FILAMENT WHICH CONSISTS OF COCOON FIBER AND SYNTHETIC ONEHiroyuki Ogawa, Kazuo Matsuda, Takebi Daikuhara1966 Volume 22 Issue 6 Pages 285-288
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSThe mono-filament of synthetic fiber was fed as the core filament under the suitable tension to the have end feeder of reeling machine. In the formation of the compound filament, the cocoon fibers surround the core filament and adhere to it by their sericin. Our purpose is to obtain a filament which has characteristics of both the cocoon fiber and synthetic one.
1) The feed tension of the mono-filament of synthetic fiber may be expressed by the following equation:
where ps: the feed tension of the mono-filament of synthetic fiber pc′: the total unwinding tension on all baves ks: the modulus of elasticity of synthetic fiber kc′: the modulus of elasticity of cooked cocoon fiber a: the denier of synthetic fiber b: the total denier of all cocoon fibers
2) Using 15 denier TETRON as the core, 45 denier compound filament was monufactured. Under the same elongation, its tenacity lies between the tenacity of synthetic fiber and that of raw silk. The compound filament has the same elongation as the synthetic fiber which has smaller one than that of raw silk.View full abstractDownload PDF (296K) -
[in Japanese], [in Japanese]1966 Volume 22 Issue 6 Pages 289-292
Published: June 10, 1966
Released on J-STAGE: November 28, 2008
JOURNAL FREE ACCESSDownload PDF (302K)
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