In this study, cast polypropylene (CPP) film (TOYOBO, PYLEN FILM-CT, P1011, Japan) was used as a base film. This CPP film was unidirectionally drawn at 1.0, 1.5, 2.5 times by uniaxial drawn machine (Nakamoto Packs Co., Ltd., Japan). At that time, these films were annealed at 80˚C, 100˚C, 120˚C to stabilize molecular orientation and drawn film. The drawn film conditions then will be referred as 1.0×, 1.5×, and 2.5×, respectively.

Figure 1 shows a schematic diagram of heat sealing method in this experiment. The uniaxial drawn and un- drawn films were placed in a bar type heat-sealing machine (Heat seal Tester, Sangyo Co., Ltd, Japan). The heat seal pressure was kept constantly at 0.2 MPa. The heat sealing time was 1.0 second. The heat sealing temperature was set to 145˚C.

In order to examine the mechanical properties of the heat sealed part, a T-peel test was carried out with test pieces of 15 mm wide and 100 mm long. A schematic draw of the heat sealed specimen is shown in Figure 2. The peel test was performed at 300 mm/min by using an INSTRON universal testing machine (INSTRON 4466) at 20˚C. The span length was 50 mm.

To examine the thermal properties of drawn sample films, a Differential Scanning Calorimeter (DSC) (Perkin-Elmer DSC, Pyris1) was utilized in the range of 40˚C to 250˚C at a heating rate of 20˚C/min under a nitrogen gas purge. The temperature and heat of transition obtained by the instrument were calibrated with indium and zinc standards before the measurements.

Heat sealed part of specimens were mapping by microscopic FT-IR (Frontier-Spotlight 400: Perkin Elmer, Japan) to evaluate the crystallinity and the orientation of heat sealed parts with and without heat sealing. Mapping mode was transmittance imaging method. Wave resolution was 4 cm⁻¹ with 2 scans. Pixel size was set to 25 μm.

Raman spectra have been measured with the micro-Raman backscattering geometry. The Raman spectra were excited with the linearly polarized 633 nm line of He-Ne laser (LabRAM HR-800: HORIBA Co., Ltd., Japan). The excitation beam was directed to the sample compartment of a properly modulated metallurgical microscope (Olympus BX-41). The microscope was used for the delivery of the excitation laser beam on the sample and the collection of the backscattered light through a beam splitter with objective lens adapted to the aperture of the microscope. Exposed time was set to1.0 s. The number of scan was set to 5 times.

Figure 3 shows the peel strength of drawn film specimens at various stabilization temperatures. Peel strength of cast PP film was about 10 N. All of peel strengths for the drawn films indicated lower than that of cast PP film. The peel strength was decreased with increasing the drawn ratio for the PP film, while the peel strength was decreased with increasing the stabilization temperature for 1.0× and 2.5× drawn films although the peel strength of 1.5× drawn film was slightly increased with increasing the stabilization temperature. The peel strength for 1.5× drawn film showed around 3 N/15mm, while the peel strength for 2.5× drawn film showed about only 1

N/15mm, and the strength reduced to approximately 30%. This is caused by the high molecular orientation degree in PP film as compared with low drawn ratio films such as 1.0× and 1.5×. As a result, it was hard to heat seal for 2.5× drawn film. Thus, it is considered that there is a linear relationship between drawn ratio and peel strength, that is, depending on the orientation degree of PP molecules in the films.

We tried to perform DSC measurement in order to evaluate the change in crystallinity of higher order structure at heat sealed part of the PP drawn films. Figure 4(a) and Figure 4(b) shows the typically DSC curves of CPP film and 2.5× drawn PP film at 145˚C heat sealing temperature, respectively. Melting temperature and melting enthalpy (ΔH) value of the 1st and the 2nd heating thermogram of CPP film are similar, while melting point of the 1st heating thermogram of 2.5× drawn film exhibited higher value as compared with the 2nd one. This difference depends on the drawn ratio of PP film, which influenced on differences in the molecular orientation of PP films. ΔH values of the films and heat sealed films at each heat sealing condition are shown in Figure 5. It was found that ΔH of non-heat sealed film was lower than heat sealed part due to a higher crystallinity of the heat sealed part as compared with the non-heat sealed part. In addition, ΔH of higher drawn ratio was lower than that of lower drawn ratio. It was attributed to the crystallization of the film after heat sealed. It can be considered that ΔH of higher drawn ratio film becomes low due to the energy waste to make it relaxation of the molecular orientation in PP films. Accordingly, these results will support the change in the secondary order structure of PP films. However, in the results of DSC measurement, it is very difficult to obtain the precise and information on secondary structure change in the edge area of heat sealed part. Hence, we applied the micro FT-IR mapping for heat sealed edge part of PP film for better understanding.

Figure 6 shows a typical FT-IR spectrum of PP film. Generally, the 998 cm⁻¹ and 841 cm⁻¹ bands are associated with long repeating monomer units in the crystalline 3₁ helix of PP. The short helix segments are associated with the 972 cm⁻¹ band of the FT-IR spectrum. There is a linear correlation between the intensities of the 998 cm⁻¹ and 841 cm⁻¹ bands and the density of PP as a measure of its crystallinity. Therefore, the crystallinity of PP can be determined by the ratio of the 998 cm⁻¹ and 972 cm⁻¹ absorption bands [10] [11] . Figure 7 and Figure 8 shows the CCD optical images and illustrate the FT-IR mapping images of PP film of heat sealed edge part. These mapping images were normalized at 972 cm⁻¹ and imaged the peak ratio for 998 cm⁻¹/972cm⁻¹ as shown in Figure 6. The left area corresponds to non-heat sealed part and the right area corresponds to heat sealed part in each image in Figure 8. From the result, light color corresponds to the higher crystallinity area. In non-heat sealed part, crystallinity was increased with increasing the stabilization temperature so that the color variation is consistent with the molecular orientation of PP film. Because drawn film could raise the creep relaxation without heat stabilization after drawing. Therefore, crystallinity of non-heat sealed part of PP film was decreased

with decreasing the stabilization temperature. On the other hand, similar tendency was shown in the heat sealed part of PP film, that is, crystallinity of heat sealed part was increased with increasing the stabilization temperature. However, in this case, it was seen that each crystallinity was lower as compared with non-heat sealed part. Because it is considered that the thermal energy of heat sealing is used for the relaxation of molecular orientation in PP films. As a result, the crystallinity of heat sealed part is lower than non-heat sealed part. In addition, the crystallinity of the edge part of heat sealing indicated the different tendency as compared with heat sealed and non-heat sealed part. It is very interesting and important phenomena of heat sealed films.

Figure 9 presents the Raman spectra of PP film for each drawn film. After drawing, some peaks were suppressed, where is considered that these peaks are corresponding to molecular orientation in PP films. In this study, the peak ratio (I₈₄₈/I₈₁₈) was calculated in order to evaluate molecular orientation and/or crystallization changes near heat sealed edge part, and then the result was plotted in Figure 10. The peak ratio of neat film was higher than heat sealed part in Figure 10(a). The slope of strength change was observed in the interface area within 200 µm. As the resolution and the pitch width of microscopic Raman spectroscopy are 1 µm and 1 µm respectively, it was found that the molecular orientation of PP films indicated the relaxation over an appreciable range of the slope gradually. It should be noted that when this slope is rapidly steep, stress concentration will arise at this edge part for tensile loading. In Figure 10(b), the difference of Raman intensity was not indicated for each stabilization temperature, although the intensity at stabilization temperature 120˚C became slightly coarse because of the relaxation of molecular orientation by the heat sealing energy. However, the degree of relaxation for 2.5× drawn film is very little as compared with 1.5× drawn film, and the heat sealing energy of 1.0 s and 145˚C is insufficient to relax the molecular orientation of 2.5× film. As a result, it is clarified that the peel strength of the film indicated the low value as shown in Figure 3.