International Journal of Experimental Spectroscopic Techniques
Volume 1, Issue 1
Research Article DOI: 10.35840/2631-505X/8501
Raman Spectroscopic Study of High-density Polyethylene during Tensile Deformation
Takumitsu Kida, Yusuke Hiejima* and Koh-hei Nitta
Table of Content
Figure 1: Schematic illustrations of (a) insitu Raman spectroscopic...
Schematic illustrations of (a) insitu Raman spectroscopic system with the tensile tester; (b) HDPE specimens during tensile testing. The red spot on each specimen represents the laser spot.
Figure 2: Raman spectrum of undrawn HDPE specimen...
Raman spectrum of undrawn HDPE specimen.
Figure 3: Raman spectra (circles) of undrawn specimen...
Raman spectra (circles) of undrawn specimen. The red line represents the fitting with a sum of Voigt functions (blue lines).
Figure 4: Schematic illustrations of (a) typical stress-strain...
Schematic illustrations of (a) typical stress-strain curve of HDPE; (b) macroscopic deformation of HDPE specimen. A: first yield point, B: second yield point, C: initiation of neck propagation, D: onset of strain hardening.
Figure 5: Stress dependences of peak shifts of...
Stress dependences of peak shifts of highly-oriented HDPE specimen under tension for Raman bands assigned to (a) crystalline; (b) amorphous chains.
Figure 6: Strain dependences of peak shifts of Raman...
Strain dependences of peak shifts of Raman bands assigned to (a) crystalline and (b) amorphous chains under uniaxial stretching.
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Takumitsu Kida, Yusuke Hiejima* and Koh-hei Nitta
Department of Chemical and Materials Science, Kanazawa University, Kakuma Campus, Kanazawa 920-1192, Japan
Y. Hiejima, Department of Chemical and Materials Science, Kanazawa University, Kakuma Campus, Kanazawa 920-1192, Japan, E-mail: email@example.com
Accepted: January 22, 2016 | Published Online: January 25, 2016
Citation: Kida T, Hiejima Y, Nitta K-H (2016) Raman Spectroscopic Study of High-density Polyethylene during Tensile Deformation. Int J Exp Spectroscopic Tech 1:001.
Copyright: © 2016 Kida T, et al. This is an open-access article distributed under the terms of the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original author and source are credited.
In situ Raman spectroscopy is applied to high-density polyethylene to elucidate the microscopic deformation mechanism during uniaxial stretching. The peak shifts of the C-C stretching modes of the amorphous chains show remarkable red shifts in the elastic region, where as the red shift of the C-C stretching vibration along the crystalline chain begins after the first yield point, suggesting that the stretching stress is concentrated on the amorphous chains before the first yield point. The C-C stretching vibrations perpendicular to the crystalline chain, as well as the CH2 bending modes, show blue shifts in the yielding region, which is explained by the compression stress due to the densification of lamellar cluster units. After the yielding region, the orthorhombic crystalline structure is slightly expanded, and the stretching stress is applied on the crystalline and amorphous trans chains.
Raman spectroscopy, Polyethylene, Peak shift, Load sharing, Tensile deformation
Semi-crystalline polymers, such as high-density polyethylene (HDPE) have a variety of structures over a wide range of length scale. The supramolecular structures are spontaneously formed through complicated crystallization processes; the molecular chains are partially folded to form the lamellar crystals, followed by the radial growth of the lamellar crystals to form spherulites. It has been revealed that the hierarchical structures are responsible for the mechanical properties of semi-crystalline polymer solids such as strength and toughness .
It has been demonstrated that tensile deformation of semi-crystalline polymer results in various structural changes . Undrawn specimen has isotropic spherulitic structure which are collapsed during the yielding, and further drawing results in formation of fibrillar structures [3,4]. The mechanism of deformation has been investigated with various experimental methods [5-8]. For polymeric materials, the stress relaxation of specimen after unloaded from the mechanical testing machine results in appreciable structural changes . Then, in situ spectroscopic observation during mechanical testing has a crucial role for investigation of microscopic mechanism of deformation.
Raman spectroscopic analyses have been applied for various materials, such as nanoparticles and polymer composites [10-16]. Rheo-optics which is methods of simultaneous measurements of spectroscopic observation and mechanical testing are powerful tools for investigation of deformation mechanism of polymeric materials. The rheo-optical apparatuses for the birefringence and the infrared (IR) absorption have been developed and applied to clarify the deformation mechanism of polyolefins [17,18]. Since the IR spectroscopy provides the molecular orientation of the amorphous chains as well as the crystalline chains, in situ IR spectroscopy has been applied for the uni- and biaxial deformation of films [19-21]. In radiation facilities, in situ small- and wide-angle X-ray scattering measurements have been conducted, and real-time monitoring of the crystalline orientation and the change of the crystallinity during elongation has been reported [22,23].
Since the vibrations of the skeletal C-C bonds are strongly Raman active, the microscopic environments of the polymer chains are probed by the Raman spectroscopy. It has been demonstrated that the spectral shift of Raman bands are interpreted as the microscopic stress applied on the polymer chains [24,25]. Raman spectroscopy has been utilized for determination of the morphology and the crystalline modulus of semi-crystalline polymers of undrawn and highly-drawn specimens under tension [7,24,26-28]. In situ observation of the load sharing on the polymer chains by monitoring the peak shift is quite limited, and the discussion on the microscopic structural changes relies only on a few Raman bands such as the C-C stretching and the CH2 rocking modes [9,26,27,29].
In this study, we have conducted the rheo-Raman spectroscopy for HDPE under uniaxial tensile test. The spectral shifts of several Raman bands assigned to the crystalline and amorphous phases are obtained simultaneously. By combining with the peak shifts in the highly-oriented HDPE specimen under tension, microscopic deformation mechanism of HDPE is discussed.
Ziegler-Natta-catalyzed HDPE pellets (Mw = 10 × 104, Mw/Mn = 5.9) were used. The pellets were melted in a laboratory hot press for 5 min at 483 K and 10 MPa and then quenched in iced water, to prepare a sheet with a thickness of about 1 mm. The sample sheets were annealed in an oven at 353 K for 5 h. The density of the sample was determined by the Archimedes method and its volumetric crystallinity was determined from the density, where the densities of the amorphous and the crystalline regions were assumed to be ρa = 855 kg/m3 and ρc = 1000 kg/m3, respectively . The test specimens were cut out of the sample sheet with a notch-shaped die (2 mm gauge length, 4 mm width) shown in Figure 1(a). Highly-oriented specimens were prepared as follows. The HDPE specimen was drawn at 373 K up to the strain of 2, and held for 10 min, then left at room temperature for 1 day.
The apparatus for the rheo-Raman spectroscopy is shown schematically in Figure 1(b). A custom-made tensile tester with a double-drawing mechanism was installed in the Raman spectroscopic apparatus. Laser light from a DPSS laser (LASOS, Jena, Germany, 637.9 nm in wavelength, 200 mW in laser power) was monochromated with a laser line filter, and irradiated into the notched portion of the specimen, with a spot size of 1 mm in diameter. Since the two grips of the tensile tester move toward the opposite directions at the same rate, the center of the specimen was irradiated during the entire tensile testing. It is also noteworthy that the necking of the specimen is always initiated at the center of the notch-shaped specimen. The elongation speed was set to 1 mm/min, and the stretching temperature was 20°C. The scattered light was collected with a pair of convex lenses, where the excitation light was removed with a Raman long-pass filter. A charge-coupled device camera equipped with a monochromator (PIXIS 100 and SpectraPro 2300i, Princeton Instruments, Trenton, USA, NJ) was used as the detector. The Raman spectra were accumulated 10 times with an exposure time of 500 ms (Figure 2).
The peak shift is defined as the deviation of the Raman shift from that of the undrawn specimen:
Where the subscript 0 denotes the undrawn specimen. It has been observed that the IR and Raman bands show substantial shifts during deformation [24,25,31].The anti-symmetric (1063 cm-1) and symmetric (1130 cm-1) C-C stretching modes are the vibrations of the skeletal chains parallel and perpendicular to the chain axis, respectively. Then, the peak shifts of the C-C stretching modes have been used to detect the load sharing on the polymer chains [7,26]. Although the Raman band at 1080 cm-1 assigned to the C-C stretching mode of the amorphous chains only shows broad and weak peak as seen in Figure 3(a), sufficiently high S/N ratio of the present system enable us to fit the Raman band successfully.
Three distinctive peaks around 1400 cm-1 are assigned to the CH2 bending modes. Since the 1418 cm-1 band assigned to the CH2 bending in the orthorhombic crystal is classified into the space group of Ag, this band is used to estimate the orientation of the crystalline chains [32,33]. The 1418 cm-1 band is also useful for estimation of the crystallinity of polyethylene [34-36]. The 1440 cm-1 and 1460 cm-1 bands are assigned to the CH2 bending modes of the amorphous trans chains and the melt-like amorphous chains, respectively [35,37]. It is proposed that the former chains exist in the intermediate phase between the crystalline and amorphous regions with in the three-phase model [38,39].
The Raman bands at 1298 cm-1 and 1313 cm-1 are assigned to the CH2 twisting modes of the crystalline and amorphous chains, respectively. These bands are commonly used as the internal standards to estimate the crystallinity [34,40], and molecular orientation [32,41].
Results and discussion
Characterization and Raman spectra of unstretched specimen
The density and the volumetric crystallinity were determined to be 951 kg/m3 and 66%, respectively. The Raman spectrum of the undrawn HDPE specimen was shown in Figure 2 and the assignments for the Raman bands was listed in Table 1 [32,33,42,43]. The Raman bands for the crystalline chain (1063, 1130, 1298 and 1418 cm-1) and the amorphous chain (1080, 1440 and 1460 cm-1) were used in the following analysis. As shown in Figure 3, each Raman band was successfully fitted with a sum of Voigt functions using a nonlinear Levenberg-Marquardt method.
Stress-strain behavior of HDPE
In Figure 4, a typical stress-strain curve and the shapes of specimen during uniaxial stretching are shown for HDPE. Before the first yield point (denoted as A) at which the stress shows a maximum, the specimen is deformed homogeneously. Beyond the first yield point, the stress decreases and shear bands appear in the notched portion of the specimen. Around the second yield point (B), a concave construction is developed in the central portion of the specimen, and an inhomogeneous deformation called necking initiates between B and C. After the yielding region, the necked portion propagates towards the both ends of the specimen (D). After the neck-propagation is completed, the increase of the stress resumes in the strain-hardening region.
Raman spectral shifts of highly-oriented HDPE under tension
Figure 5 shows the stress dependences of the peak shifts of Raman bands assigned to the crystalline and amorphous chains of the highly-oriented HDPE specimen. Because the crystalline and amorphous chains in highly-oriented specimens are oriented toward the stretching direction, it is suggested that these peak shifts are induced by the tensile stress applied along the crystalline and amorphous chains.
The two Raman bands at 1063 and 1130 cm-1 assigned to the crystalline chains show obvious red shifts under stretching, and the shift factors α (slopes of Figure 5) are determined to be -11.3 cm-1/MPa and -7.7 cm-1/MPa, respectively. These values are in good agreement with those reported previously [7,24]. On the contrary, the Raman bands assigned to the C-C twisting and the CH2 bending modes show substantially smaller shifts factors (α1298 = -2.2 cm-1/MPa, α1440 = -5.5 cm-1/MPa, α1460 = -5.2 cm-1/MPa) than the C-C stretching modes, indicating that the torsional motions of the main chain and the librational motions of CH2 groups are less affected by the stretching stress. The difference of the sensitivity to the stretching of a single chain has also been predicted from the lattice dynamical calculations [25,31]; their calculation has demonstrated that the applied stress is concentrated on the C-C stretching and the C-C-C bending modes, and that the vibrations of the pendant H atoms are not affected. The blue shifts of the C-C stretching and twisting modes as well as the CH2 bending modes have been observed in ultra-high-molecular-weight polyethylene under hydrostatic pressure, which have been interpreted as the hindrance of the vibrational motions by the compression due to dense packing under high pressures .
The shift factor of the CH2 bending mode of the orthorhombic crystalline chains is found to be practically zero (α1418 = -0.06 cm-1/MPa). From the WAXS experiments , it is found that the 1418 cm-1 band strongly depends on the cross section of the unit cell of the orthorhombic crystal, where blue shift is observed for smaller cross section. Since the 1418 cm-1 band also shows red shift under hydrostatic pressure , it is plausible that the competition of these two effects cancel out the pressure dependence of α1418.
Raman spectral shifts of the HDPE during tensile deformation
The strain dependences of peak shifts of various Raman bands of HDPE during tensile test are shown in Figure 6 along with the stress-strain curve of HDPE. As shown in Figure 4, the deformation of specimen proceeds from the elastic region (up to the first yield point) to the yielding region (up to the neck-initiation), followed by the strain-hardening region (after neck-propagation). It is noteworthy that the necking region is quite narrow for the notch-shaped specimens. In accordance with these deformation stages, each Raman band show characteristic shifts as discussed in the following subsections, except for the 1298 and 1313 cm-1 bands which are insensitive to deformation.
C-C stretching modes (1100 cm-1 range)
In the elastic region, the peak shifts of the 1063 and 1130 cm-1 bands assigned to the C-C stretching modes of the crystalline chains remain zero, suggesting no stress is applied on the crystalline chains. On the contrary, the 1080 cm-1 band assigned to the C-C stretching modes of the amorphous chains shows drastic red shift, and the shift linearly increases with the strain. Then, it is suggested that the stretching stress is concentrated only on the amorphous chains [45-47]. After the first yield point, Δν1063 begins to decrease with the strain, suggesting the increase of the stretching stress applied along the crystalline chains. On the other hand, Δν1130 shows a sharp rise and has a maximum around the second yield point, which has been interpreted with the compression due to the densification of the lamellar cluster units [48,49]. After the second yield point, Δν1130 drops and Δν1063 shows a narrow plateau, suggesting that the microscopic stress imposed on the crystalline chains is released. The red shift of the 1080 cm-1 band also slightly decreases, suggesting that the plastic deformation such as the reorientation of the lamellar cluster units [26,48,49] leads to decrease of the overall stress level in the amorphous phase as well as the crystalline phase. In the strain-hardening region, all of the Raman bands at 1063, 1080 and 1130 cm-1 show red shifts weakly dependent on the strain, suggesting that almost constant stretching stress is applied on both of the crystalline and amorphous chains after the plastic deformation is completed.
CH2 bending modes (1400 cm-1 range)
In the elastic region, the peak shifts Δν1418, Δν1440 and Δν1460 for the CH2 bending modes remain zero, as shown in Figure 6. After the first yield point, Δν1440 and Δν1460 for the amorphous chains sharply increases with the strain, and show a maximum around the second yield point, suggesting the hindrance of the CH2 bending motions. Around the first yield point, Δν1418 begins to deviate from zero and has a shallow minimum around the second yield point, which is interpreted as the narrowing of the crystalline lattice. These peculiar behaviors in the yielding region are explained by the compression stress caused by the densification of lamellar cluster units [48-50]. Since the 1460 cm-1 band assigned to the amorphous chains shows larger blue shifts than the 1440 cm-1 band assigned to the trans chains in the intermediate phase, the compression stress seems to be mainly imposed on the amorphous phase. After the second yield point, Δν1418 shows a steep rise, suggesting the expansion of the orthorhombic crystal cell. In the strain-hardening region, Δν1460 is practically zero, suggesting no stress is applied on the amorphous phase. In spite of the relatively small shift factor, the 1440 cm-1 band shows large red shift, implying the amorphous trans chains such as tie molecules [43,44] are extremely stretched.
In situ Raman spectroscopy was applied to HDPE under uniaxial stretching, and the spectral shifts of several Raman bands assigned to the crystalline and amorphous chains were obtained during the elongation process. By combining these peak shifts which provided information on the changes in the microscopic environment of each mode, deformation mechanism was discussed. In the elastic region, only the C-C stretching mode of the amorphous chains showed red shift, suggesting the stretching stress was loaded on the amorphous chains. After the first yield point, the stretching stress along the crystalline chains increased with the strain. Between the first and second yields, the compression stress due to the densification of the lamellar cluster units was imposed both on the crystalline and amorphous phases. After the second yield point, where the lamellar cluster units began to orient toward the stretching direction, the compressive stress was released, accompanied by the slight expansion of the orthorhombic crystal. In the strain-hardening region, the stretching stress along the crystalline and amorphous trans chains increased, implying the tie molecules are extremely stretched.
This work is financially supported by JSPS KAKENHI (Grant Number 26410221).