International Journal of SpectroscopyVolume 2013 (2013), Article ID 720598, 6 pageshttp://dx.doi.org/10.1155/2013/720598

Research Article

Identification of LDPE Grades Focusing on Specific CH₂ Raman Vibration Modes

Richard Jumeau,1,2 Patrice Bourson,¹ Michel Ferriol,¹ François Lahure,² Marc Ponçot,³ and Abdesselam Dahoun³

¹LMOPS E.A. 4423, Université de Lorraine Supelec, 57070 Metz, France²Total Plateforme de Carling–Saint-Avold, 57501 Saint-Avold, France³Science Engineering of Materials and Metallurgy Department, IJL, UMR 7198 CNRS, Ecole des Mines de Nancy, Université de Lorraine, 54042 Nancy, France

Received 20 January 2013; Accepted 12 March 2013

Academic Editor: Jin Zhang

Copyright © 2013 Richard Jumeau et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

The possibilities of applications of vibrational spectroscopy techniques (Raman spectroscopy) in the analysis and characterization of polymers are more and more used and accurate. In this paper, our purpose is to characterize Low Density Poly(Ethylene) (LDPE) grades by Raman spectroscopy and in particular with CH₂ Raman vibration modes. With temperature measurements, we determine different amorphous and crystalline Raman assignments. From these results and on the basis of the evolution of CH₂ bending Raman vibration modes, we develop a phenomenological model in correlation with Differential Scanning Calorimetry and in particular with crystalline lamella thickness determination.

1. Introduction

Nowadays, almost 30% of the plastics world production is dedicated to poly(ethylene) (PE) (77 million tons per year) [1]. This polyolefin is considered as a consumer polymer due to its moderate cost of manufacturing and its physical and mechanical properties compatible with various applications in everyday life. Indeed, PE is generally easily processable. It possesses an excellent electric insulation and shock resistance combined with a very good chemical and biological inertia [2].

For each PE grade corresponds of specific applications, presenting different rheological properties. It is then essential to know how to distinguish these products by adapted methods of characterization. Moreover, to be competitive, PE production should be analysed on-line in order to quickly give the main properties of product (Melt Flow Index, additives, flaws, etc.).

Raman spectroscopy is an innovative experimental technique of polymer process analysis, which allows doing this. Its use is nowadays growing fast because of advantages. It is a nondestructive method, capable of also giving useful information about the morphology of the polymer. This technique can be perfectly used in industry by means of adapted sensors and devices with more and more reduced dimensions [3]. Raman spectroscopy is used to determine the characteristic transition phases of PE and information about the polymer microstructure [4]. By the use of chemometric tools, for instance, it is possible to identify various Low Density PolyEthylene (LDPE) grades.

Polyethylene crystallization can be considered as the transition between fully entangled Gaussian chains and fully extended chain without entanglements ordered in manner to provide crystals. Between two ideal states, “metastable” crystalline and molten states exist [5]. Moreover, it is well known that polyethylene usually crystallizes in an orthorhombic lattice which contains two chains per unit cell with different orientation with respect to each other [6].

Strobl and Hagedorn [7] first proposed using Raman spectroscopy to characterize the three-phase morphological structure of semicrystalline polyethylene. Then, many other authors use Raman spectroscopy to determine the amount of crystallinity of polyethylene [8, 9]. Lagaron [10] presents the analysis of the changes in position of the so-called Raman crystallinity band of polyethylene, that is, 1415 cm⁻¹ Raman band, as a function of temperature, cold drawing, and material density and its interpretation is also presented. However, few studies are about microstructural attribution of CH₂ Raman bands. Raman spectroscopy is very sensitive to strain [11], so this work aims to attribute mechanically CH₂ Raman bands, consolidate the Raman three-phase analysis method, and confirm the correlation of Raman crystallinity ratio with other analytical methods.

2. Experimental

To cover a wide range of products, several grades of Low Density PolyEthylene (LDPE) were studied. In the following, they will be designated by letters A to H, from the most viscous (A) to the least viscous (H). Grades A, C, F, and H were particularly investigated to depict the trends. The choice of these products was made on the basis of relative viscosity, from the most viscous to the least viscous; in particular the mechanical properties and applications of these materials depend on their viscosity, as the examples given in Table 1.

Table 1: Designation of the studied samples.

Name
Relative viscosity (from 1 to 100)
Additives
Applications

A
1
No
Film, blowing

B
1
Yes
Film, blowing

C
3
No
Film, molding

D
3
Yes
Film, molding

E
5
No
Film, coating, molding

F
10
No
Film, coating, molding

G
30
No
Injection, molding

H
100
No
Injection, molding

The Raman spectra were obtained with a Horiba Jobin-Yvon Aramis spectrometer operating with an excitation wavelength of 532 nm, a grating with 1800 lines/mm, a 200 μm confocal hole, and a x50 lens. The studied spectral range extended from 640 cm⁻¹ to 1700 cm⁻¹. The acquisition time was 2 seconds and in order to obtain a good signal-to-noise ratio, three spectra were averaged.

The calorimetric tests were made by Differential Scanning Calorimetry (DSC) with DSC 200 F3 Maia from Netzsch. It is a heat flux apparatus able to work down to −170°C thanks to a supply of liquid nitrogen within the thermostated chamber swept by nitrogen and regulated with an intracooler. The tests were performed in pierced aluminum crucibles with a sample mass of about 20 mg. For the preliminary and detailed study of the grades A and H, the temperature program used is given in Table 2. The rate was 10°C/min for each temperature ramp.

Table 2: Temperature program for the grades A and H studied in DSC.

Rise
Start
End
Isothermal (5 min)

1
25
−150

2

−150

3
−150
150

4

150

5
150
−150

6

−150

7
−150
150

8

150

9
150
25

The thickness of crystalline lamella can be calculated with the formula of Thomson and Gibbs [12] as follows: with [13] being thickness of the crystalline lamellar, being energy of surface of the principal facets of ends of the crystalline lamella (0.070 J/m²), being melting enthalpy of the perfect crystal (2.905.10⁵ J/kg⁻¹), being density of the perfect crystal (1000 kg/m³), being theoretical melting point of the lamella of infinite size (143.5°C), and being melting point of the lamella.

3. Results and Discussion

In a first step, the various signatures of PE were determined in order to exactly identify and know the identification of the peaks of amorphous and crystalline phases. Measurements were performed as a function of temperature in order to highlight the specific Raman modes related to the different phases and their transformations [14]. Figure 1(a) shows the evolution of the part of the Raman spectrum corresponding to C–C bonds vibrations of LDPE. The right side of the figure gives typical examples of spectra recorded at room temperature (Figure 1(b), semicrystalline state) and above (Figure 1(c), amorphous state).

(a)

(b)

(c)

Figure 1: (a) Evolution with temperature of the Raman spectrum corresponding to LDPE C–C vibrations. (b) Spectrum recorded at room temperature (semicrystalline material) and (c) spectrum recorded above (amorphous material).

Now, we would like to focus on the bands related to the CH₂ group, (Figure 2(a)). After comparison with the phase at high temperature (purely amorphous), we can fit this part of the spectrum at room temperature with four peaks using three Lorentzian and one Gaussian functions, respectively, assigned to the crystalline phase (c-CH₂) and the amorphous phase (a-CH₂). The existence of three peaks for the crystalline phase can be interpreted by considering that in a Raman spectrum, and the position of bands depends on the state of strains and the environment of the chemical bonds [15–20]. A shift towards low frequencies corresponds to an elongation of the bond, whereas a shift towards high wave numbers to a compression.

(a)

(b)

Figure 2: (a) Fitting of the LDPE CH₂ spectrum at room temperature with three Lorentzian functions (corresponding to the crystalline phase) and a Gaussian function (corresponding to the amorphous phase); (b) representation of the LDPE lamellar semicrystalline structure.

Thus, one can assume that A band, located at 1432 cm⁻¹, corresponds to a nonstressed situation like that observed for the amorphous phase at the same frequency. The B band observed at 1411 cm⁻¹ would correspond to an elongation of the bond observed with a lower frequency and the C band at 1460 cm⁻¹ to a more compressed state of the CH bonds in CH₂ groups.

Then, these three bands correspond to three CH₂ different families in the crystalline phase of LDPE.

In a following step, we have attempted to relate these results to the viscosity of LDPE. Figure 3 shows the evolution of the integrated intensity area of the three CH₂ bands of the crystalline phase according to the different LDPE grades (from viscous to flowing grades). It can be noticed that the relative intensity of the three peaks evolves as a function of the viscosity of the LDPE grades: the integrated intensity of the band corresponding to the compressed CH₂ increases whereas that corresponding to the neutral CH₂ decreases.

Figure 3: Trend of the evolution of the integrated intensity areas of the three CH₂ bands according to the different grades (from viscous to flowing).

It is possible to relate these results to the lamellar semicrystalline structure of LDPE (Figure 2(b)). Indeed, in this structure, classically based on crystal lamella formed by the folding of polyethylene macromolecules, three kinds of CH₂ groups, elongated, compressed, and neutral, can be estimated to exist which is consistent with the preceding attribution of Raman frequencies. As schematized in Figure 4, the elongated bonds are located in the folding zone whereas the compressed bonds are located in the middle of the lamella. The compression would be due to stronger Van der Waals interactions in this zone. The neutral zone is comprised between these two other domains.

Figure 4: Representation of the lamellar crystal structure and position of the three kinds of CH₂ groups (the black lines represent the C–C skeletal structure; CH₂ bonds are perpendicular to these lines).

In the classical two-phase model, representative of the semicrystalline structure of LDPE, the periodicity of the structure is described by the long period with ( is thickness of the amorphous zone and is thickness of the crystal lamella). In a first approximation, one can consider that the viscosity partly depends on the ratio of the thickness of amorphous and crystalline phases. Then, if the long period is assumed constant, a decrease of viscosity will be traduced by an increase of the thickness of amorphous zones and a decrease of that of crystalline lamella (Figure 5). This will undergo changes in the amounts of neutral, compressed, and elongated CH bonds in CH₂ groups and therefore changes in the evolution of integrated intensity areas of the corresponding Raman peaks as shown in Figure 3. When the viscosity decreases, the relative proportion of neutral and elongated bonds tends to decrease whereas that of compressed bonds increases (the crystalline lamella thickness decreases) undergoing the subsequent decrease or increase observed for the relative integrated intensity areas.

(a)

(b)

Figure 5: Schematic representation of the LDPE structure in case of (a) viscous grade and (b) flowing grade.

Figure 6 gives crystal lamella thickness determined by DSC for several LDPE grades from viscous to flowing grades. It shows well a reduction of crystal lamella thickness as the grade is more flowing. Thus, this behaviour validates the assumptions made to interpret the evolution of the Raman spectrum and its relations with the structure of the LDPE material investigated.

Figure 6: Crystal lamellar thickness determined by DSC for several LDPE grades (from viscous to flowing grades).

Consequently, this induces in the interphase, between the amorphous and crystalline phases, more interactions and connections, which can be at the origin of the presence of a mesophase. This involves more bridging and of this fact an increase of the connections known as compressed like observed in Figure 3.

4. Conclusion

In this work, using Raman spectroscopy, a model based on the LDPE semicrystalline structure and involving the presence of three kinds of CH₂ groups in the crystal lamella, has allowed for distinguishing various LDPE grades (from viscous to flowing material). Indeed, Raman spectroscopy proved its efficiency as being very sensitive to weak variations of the environment of the CH chemical bonds. This simple study of CH₂ chemical bands of the LDPE grades can be used to predict the mechanical behaviour or rheological properties (viscosity) of this polymer.

Conflict of Interests

The coauthors have not a direct financial relation with the commercial identities mentioned in this paper (Netzsch DSC 200 F3 Maia and Horiba Jobin Yvon Aramis systems).

Acknowledgments

The authors wish to thank the teams of Total who prepared the polyethylene sampling and for the financial support.

References

Plastics Europe, “Analyse de la production, de la demande et de la valorisation des matières plastiques en Europe en 2009,” Activity Report, 2009, http://www.plasticseurope.org/.

F. Addiego, Caractérisation de la variation volumique du polyéthylène au cours de la déformation plastique en traction et en fluage [Ph.D. thesis], Institut National Polytechnique de Lorraine, Science et Ingénierie des Matériaux, 2006.

J. Martin, Etude par spectroscopie Raman du polypropylène isotactique au cours de sa déformation uniaxiale [Ph.D. thesis], Université Paul Verlaine de Metz, Science des Matériaux, 2009.

R. Jumeau, “Comparative study of various grades of polyethylene by differential scanning calorimetry (DSC) correlated with Raman spectroscopy,” AIP Conference Proceedings, vol. 1353, pp. 791–796, 2011.

S. Yamazaki, “Role of entanglement in nucleation and ‘melt relaxation’ of polyethylene,” Polymer, vol. 43, no. 24, pp. 6585–6593, 2002.

R. J. Young, in Introduction to Polymers, p. 157, Chapman and Hall, London, UK, 1983.

G. R. Strobl and W. Hagedorn, “Raman spectroscopic method for determining the crystallinity of polyethylene,” Journal of Polymer Science Part B, vol. 16, no. 7, pp. 1181–1193, 1978.

M. Kim, J. Noh, and H. Chung, “Comparison of near-infrared and Raman spectroscopy for the determination of the density of polyethylene pellets,” Analytica Chimica Acta, vol. 632, no. 1, pp. 122–127, 2009.

A. Bertoluzza, C. Fagnano, M. Rossi, A. Tinti, and G. L. Cacciari, “Micro-Raman spectroscopy for the crystallinity characterization of UHMWPE hip cups run on joint simulators,” Journal of Molecular Structure, vol. 521, no. 1–3, pp. 89–95, 2000.

J. M. Lagaron, “On the use of a Raman spectroscopy band to asses the crystalline lateral packing in polyethylene,” Journal of Materials Science, vol. 37, no. 19, pp. 4101–4107, 2002.

L. S. Schadler, S. C. Giannaris, and P. M. Ajayan, “Load transfer in carbon nanotube epoxy composites,” Applied Physics Letters, vol. 73, no. 26, pp. 3842–3844, 1998.

G. Teyssèdre, Caractérisation des Polymères par Analyse Thermique, Traité Analyse et Caractérisation, Techniques de l’Ingénieur, 1996.

B. Wunderlich, Macromolecular Physics, Academic Press, New York, NY, USA, 1976.

M. Ponçot, J. Martin, J. M. Hiver, D. Verchère, and A. Dahoun, “Study of the dimensional instabilities of laminated polypropylene films during heating treatments,” Journal of Applied Polymer Science, vol. 125, no. 5, pp. 3385–3395, 2012.

P. Colomban, “Analysis of strain and stress in ceramic, polymer and metal matrix composites by Raman spectroscopy,” Advanced Engineering Materials, vol. 4, no. 8, pp. 535–542, 2002.

A. H. Fawcett, Polymer Spectroscopy, Barnes & Noble, 1996.

C. Galiotis, R. J. Young, P. H. J. Yeung, and D. N. Batchelder, “The study of model polydiacetylene/epoxy composites—part 1: the axial strain in the fibre,” Journal of Materials Science, vol. 19, no. 11, pp. 3640–3648, 1984.

G. Gouadec, S. Karlin, and P. Colomban, “Raman extensometry study of NLM202 and Hi-nicalon SiC fibres,” Composites Part B, vol. 29, no. 3, pp. 251–261, 1998.

S. J. Spells, Characterization of Solid Polymers: New Techniques and Developments, Chapman & Hall, London, UK, 1994.

G. Gouadec and P. Colomban, “Raman Spectroscopy of nanomaterials: how spectra relate to disorder, particle size and mechanical properties,” Progress in Crystal Growth and Characterization of Materials, vol. 53, no. 1, pp. 1–56, 2007.