International Journal of Polymer ScienceVolume 2012 (2012), Article ID 549154, 9 pagesdoi:10.1155/2012/549154

Research Article

Effects of Kaolin Surface Treatments on the Thermomechanical Properties and on the Degradation of Polypropylene

Melia Guessoum,¹ Sorya Nekkaa,¹ Françoise Fenouillot-Rimlinger,² and Nacerddine Haddaoui¹

¹Laboratoire de Physico-Chimie des Hauts Polymères (LPCHP), Département de Génie des Procédés, Faculté de Technologie, Université Ferhat Abbas, Sétif 19000 , Algeria²Laboratoire des Matériaux Macromoléculaires, Institut National des Sciences Appliquées (INSA) de Lyon, Domaine Scientifique de la Doua, Bâtiment Jules Verne, 17 avenue Jean Capelle, Villeurbanne, 69621 Lyon, France

Received 1 December 2011; Accepted 11 January 2012

Academic Editor: Jan-Chan Huang

Copyright © 2012 Melia Guessoum 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 effects of kaolin content and treatments on the thermal and mechanical properties and on the degradation of polypropylene were examined using mechanical tests, differential scanning calorimetry (DSC), and thermogravimetry (TGA). The weak interactions filler/matrix have been reinforced using a modification with urea then with an ammonium salt and a surface treatment with a silane coupling agent. The XRD results showed that the peak at the d-value of 10.7 Å increases in urea/kaolin complex, but the treatment with the ammonium salt caused the return to the initial state of the clay. FTIR results showed the appearance of new bands characteristic of the interactions between urea and kaolinite and the alkylammonium and kaolinite. The mechanical properties of the composites exhibited important variations while the DSC results showed the decrease of the crystallization temperature as a function of kaolin content. TGA thermograms pointed out the improvement of the composites' thermal stability.

1. Introduction

In recent years, rapid growth and high consumption rates were predicted for various polyolefin composites, since they find applications in many areas such as automotive, home appliances, and construction. The use of mineral fillers in the fabrication of thermoplastic composites is mainly governed by price-performance relationships. Apart from reducing the price of the final material, mineral fillers can also help to improve shrinkage on moulding, stiffness and flammability, which are the principal limitations of the bulk thermoplastics. The effects of fillers on the mechanical and other properties of the composites depend on their shape, particle and aggregate sizes, surface characteristics, and degree of dispersion [1–3].

Polypropylene (PP) is one of the most frequently used polymers because of its low price, balanced properties, and easy processability. To improve some of its properties and thus widen its application range, blending with other polymers and/or fillers is the alternative that is usually employed in order to increase its strength, impact resistance and toughness. Among the inorganic fillers that are used to improve PP properties, clays are recognized to get several beneficial variations on stiffness, hardness, toughness, and heat resistance [2–4].

Kaolinite (Al₂Si₂O₅(OH)₄) is a 1 : 1 phyllosilicate containing a gibbsite octahedral layer and a silicon oxide tetrahedral sheet. This asymmetric structure allows the formation of hydrogen bonds between consecutive layers, providing a large cohesive energy. As the inorganic surface of the particles is highly polar while the PP is apolar, the interface interaction can be provided only by molecular modification of one or both components. So to get a good dispersion, the surface modification of kaolinite can be achieved either by the use of coupling agents, or by the intercalation of chemical species in the interlayer gallery, to increase the basal spacing of the clay which may facilitate the intercalation of polymer chains between its platelets [5–8].

Also, the number of the chemical species which can be directly inserted in the interlayer of the kaolinite is limited due to the great cohesive energy between the clay layers. The most known compounds that intercalate directly into kaolinite on contact with the clay are formamide, hydrazine, potassium acetate, dimethylsulphoxide (DMSO), and urea. Other compounds can also be introduced in the kaolinite interlayer by the displacement of a previously intercalated compound [9–13].

In the urea/kaolinite intercalation model proposed by Ledoux and White [14], urea forms hydrogen bonds on interacting with the silica plane and the inner surface hydroxyls via its NH₂ groups. According to Frost et al. [15, 16], urea forms hydrogen bonds with the silica plane only. Also, Makó et al. [17] proposed a structural model comprising two types of urea bonding to the siloxane surface, involving the NH₂ groups and the oxygen atom of the silica layer.

The inorganic fillers and their treatments induce variations on practically almost of the composites properties especially, mechanical and thermal characteristics. At high filler loading, it was noticed that the elastic modulus and the tensile strength increase while the deformation at break diminishes drastically due to the decrease of the deformability of the matrix [18]. The fillers affect also the crystallization behavior and the degradation process so an increase of the thermal stability of the composites compared to the virgin material is generally observed [19–21].

The aim of the present work is to study the effects of small concentrations of two types of modified kaolin, the first with an alkylammonium salt after passing by a treatment with urea and the second surface treated with a silane coupling agent, on the mechanical and thermal properties of PP composites.

2. Experimental

2.1. Materials

The polymer matrix used in this study was polypropylene “Moplen RP 320H” manufactured by Basell. It is a statistical copolymer, having a melt flow index experimentally determined to  be 2.30 g/10 min at 190°C. Urea NH₂CONH2  is a Prolabo product. The alkylammonium is a hexadecyltrimethylammonium chloride abbreviated as (HDTMA), purchased from Aldrich, and having the following chemical structure CH₃(CH₂)₁₅N(CH₃)₃Cl. The coupling agent used for kaolinite surface treatment is N-[3-trimethoxysilyl propyl] ethylene diamine commercialized by Aldrich under the abbreviation Z-6020. The used kaolinite has a micrometric dimension and the following chemical composition determined by chemical analysis, as it is reported in Table 1.

Table 1: Chemical composition (wt%) of the used kaolin.

SiO₂
50.44

Al₂O₃
28.30

CaO
1.10

MgO
0.50

Fe₂O₃
2.29

LOI (loss on ignition)
10.01

2.2. Kaolinite Treatments

The experimental method used for urea intercalation was already proposed by Letaief et al. [22]. It consists on a manual grinding in a mortar of a mixture of 5 g kaolinite and 8 g of urea for a period of 2.5 hours, followed by a mechanical grinding for 15 minutes. For urea displacement from kaolinite, the resulting material was subjected to a reaction in a solution containing the ammonium salt at a temperature of 80°C for 24 hours. After That, the clay was filtered and dried then stored. Furthermore, a part of the unmodified clay was treated with two concentrations of the silane coupling agent Z-6020, dissolved in an aqueous medium, namely 2% and 4%. Finally, the three as-treated samples as well as the unmodified kaolinite were characterized by Fourier transform infrared spectroscopy and X-ray diffraction.

2.3. Composites Preparation

The composite materials, with kaolinite amounts varying from 1 to 5 parts per hundred resin (phr), were prepared by mixing the polymer matrix and the ammonium modified and unmodified kaolinite, respectively, PP/TK and PP/UK, in a two-roll mixer at a temperature of 190°C and a mixing rate of 30 rpm for a period of 10 minutes. The same procedure was also followed to prepare PP/silane-treated kaolin composites (PP/KTS), using two clay concentrations, namely, 2 and 4 phr. After That, the obtained sheets were cut into small pieces then pelletized. For the mechanical tests samples preparation, the pelletized composites were compressed in a Davenport compression moulding machine at a temperature of 190°C and a compression pressure of 220 Kg/cm² during 5 minutes.

2.4. Measurements

2.4.1. Infrared Spectroscopy

Fourier transform infrared spectroscopy (FTIR) spectra were obtained between 500 and 4000 cm⁻¹  on a Shimadzu FTIR 8400S. Ten scans were averaged at a resolution of 4 cm⁻¹ for the solid tested samples of modified and unmodified kaolinite prepared as KBr pellets (ca. 3% by mass in KBr).

2.4.2. X-Ray Diffraction

The X-ray diffraction (XRD) study on the modified and unmodified kaolin was carried out on an XPERT apparatus using Cu-kα ( Å). All measurements were taken using a generator voltage of 45 kV and a generator current of 30 mA.

2.4.3. Mechanical Properties

Notched Izod impact strengths were measured on compressed samples using a CEAST pendulum instrument. To characterize the tensile characteristics of the hompolymer and its composites, namely, the stress and the elongation at yielding and at break (σ y and ε y) and (σ r and ε r), respectively, measurements were performed according to the norm ASTM D638, at a cross-head speed of 30 mm/min on dumbbell samples using a Zwick Material prüfung 1445.

2.4.4. Differential Scanning Calorimetry (DSC)

DSC measurements were carried out on a TA instrument, according to the following program: the specimens were first heated from ambient temperature to 250°C at 10°C/min maintained at this temperature during 5 minutes then cooled to 25°C at 20°C/min. Crystallinity was calculated according to the following equation:

A crystallization melting enthalpy of 100% crystalline PP was used [23].

2.4.5. Thermogravimetric Analysis (TGA)

The tests were performed on a TA instrument (TGA Q500) by heating the samples from 20 to 550°C at 20°C/min. From DTG thermograms giving the variations of the weight loss derivative as a function of temperature, we estimated the temperatures at which starts and finishes the degradation process and respectively, as well as and which indicate the temperature at the maximum weight loss and the residual mass, respectively.

3. Results and Discussions

3.1. Treated and Untreated Kaolinite Characterization

3.1.1. Infrared Analysis

The unmodified kaolinite FTIR spectra shows the appearance in the hydroxyl zone of the bands at the following wave numbers: 3696, 3674, 3653, and 3620 cm⁻¹. As it is reported in Figure 1(a), the three first bands characterize, respectively, the outer hydroxyl groups vibrations. Also, the observation of the bands at 3674 and 3653 cm⁻¹ confirms that the used kaolinite is a highly ordered mineral. The band at 3620 cm⁻¹ corresponds to the inner hydroxyl groups which do not participate to the establishment of the hydrogen bonds responsible of the great cohesive energy of this clay. The Si-O- and Si-O-Si vibrations are illustrated by the bands at 1114, 1030, and 1006 cm−1 whereas the Al–OH bond vibrations are visibly characterized by the bands appearing at the wave numbers 937, 912, 795, and 756 cm⁻¹. Additional broad stretching bands of kaolinite at 3400, and 1630 cm⁻¹ are attributed to the associated water adsorbed on the external surface.

Figure 1: FTIR spectra of (a) neat kaolinite, (b) urea, (c) kaolin/urea, and (d) kaolin/HDTMA.

The FTIR urea spectra (Figures 1(b)) exhibits bands between 3500 and 3100 cm⁻¹ assigned to symmetric and asymmetric stretching vibrations of the N-H bonds, at 1683, 1630 and 1603 cm−1 characterizing the C=O vibrations and a band at 1468 cm⁻¹ representing the C–N bond stretching.

The FTIR spectra of kaolinite/urea intercalate (Figure 1(c)) shows the bands at 3696 and 3620 cm⁻¹ assigned to the kaolinite hydroxyls. The rest of the hydroxyl groups bands observed for the untreated kaolinite at 3674 and 3653 cm⁻¹ are not present in this case due to the loss of hydrogen bonding between the layers. Makó et al. [17] proposed that the weakening of the 3696 cm⁻¹ band compared to the 3620 cm⁻¹ one, reflects hydrogen bonding between inner surface hydroxyls and urea molecules. Also, according to Ledoux and White [14], the new band detected at 3500 cm⁻¹ results from hydrogen bonds formation between NH₂ groups of urea and O-Si-O groups of kaolinite. In the domain 1400–1800 cm⁻¹, the changes in urea vibrations bands in kaolinite/urea intercalate can also be followed. Valášková et al. [24] observed that the stretching vibration of C=O groups is detected as for pure urea at 1683 cm⁻¹, but the formation of hydrogen bonds with kaolinite hydroxyl groups shifts the stretching frequency of urea from 1630 cm⁻¹ to 1617 cm⁻¹. Makó et al. [17] noticed that the stretching vibration of urea C=O groups, detected at 1673 cm⁻¹, is shifted to a higher wave number in kaolinite/urea intercalate. The new band that they observed at 1683 cm⁻¹ is due to the free C=O vibration since the conjugation between the C=O and NH groups no longer occurs and new hydrogen bonds are formed between the NH₂ groups and oxygen atoms of the siloxane layer. In our material, the bands attributed to the urea binding in kaolinite are detected at 1683 cm⁻¹ and 1627 cm⁻¹ in the complex. According to the model of types of urea bonding to kaolinite, proposed by Makó et al. [17], the hydrogen bonds concerns the NH₂ group attached to a free nonconjugated C=O and the oxygen atom of the siloxane layer.

After treatment with the alkylammonium salt, the spectra reported in Figure 1(d) reveals no characteristic peaks of urea molecules bonded to kaolinite groups which is the proof that they have been totally displaced during the treatment with the ammonium salt. In addition, the FTIR spectra points out the presence of two new weak bands at approximately 2920 and 2850 cm⁻¹ attributed, respectively, to the symmetric and asymmetric stretching vibrations of the – groups contained in the alkyl chains of the ammonium salt. These bands confirm the occurrence of interactions between the ammonium molecules and the kaolinite groups. The XRD results will greatly contribute to verify if these interactions involved the interlayer space functional groups or only those on the particle surface.

3.1.2. X-Ray Diffraction Results

The XRD patterns of the original and ground kaolinite are given in Figure 2: curve a in the figure displays the 001 reflection of the unmodified kaolinite at () 12.39°, the corresponding d-spacing 7.20 Å with a broad peak typical of a low-ordered kaolinite. In curve b, two overlapping XRD peaks representing two types of the expanded structure appear at around 10.7 Å, and indicate the expansion of the kaolinite ground together with the solid urea. However, a significant peak intensity is left at the d-spacing 7.20 Å, implying only some 50% efficiency. The obtained results suggest that the mechanochemical intercalation slightly deforms the lattice structure and increases the ability of the kaolinite layers to be expanded by urea. Indeed, dry grinding of kaolinite ensures intimate contact between the external surface of kaolinite and the intercalating reagent. This process favours an elastic deformation of the layers and promotes the opening of the interlayer space for the access of the guest molecules.

Figure 2: X-ray diffraction curves of neat kaolinite and kaolin/urea and kaolin/HDTMA mixtures.

Curve c of Figure 2, depicting the XRD pattern of the kaolinite treated with the alkylammonium salt in aqueous solution, shows that the treatment does not produce any detectable structural changes on the interlayer spacing of the clay. The use of the obtained kaolinite/urea complex failed in the intercalation of the ammonium salt in the interlayer gallery of the clay. So, it is clear now that the ammonium salt molecules interacted with the kaolinite hydroxyls groups involved at the surface of the clay particles and not with those situated in the interlayer space.

3.2. Composites Mechanical Characterization

3.2.1. Composites Impact Strength

The Izod impact strength variations of the PP composites notched samples filled with modified and unmodified kaolin are illustrated by Figure 3. It appears that kaolinite incorporation to the thermoplastic matrix causes a marked decrease of its impact strength. This result is explained by the fact that the introduction of the mineral filler engenders an increase of rigidity and causes a high local stress concentration at the interface filler/matrix, attributed especially to aggregates formation which weakens the strength of all the material.

Figure 3: PP composites notched Izod impact strength variations as a function of treated and untreated kaolin concentration.

Because of the prominent dominance of these effects, the ammonium kaolinite treatment effect is not apparent. However, concerning the composites filled with 2 and 4 phr of kaolinite modified with 2 and 4% of silane coupling agent, we concluded that their Izod impact strength is higher than those containing the same concentration of the unmodified kaolin, as it is reported in Table 2. This observation supports the establishment of interactions between the silane coupling agent molecules and the kaolinite superficial hydroxyl groups which contribute the get a better adhesion between the matrix and the mineral filler and allow the achievement of better composites impact strengths.

Table 2: Mechanical characteristics of PP/kaolin composites as a function of kaolin and silane concentrations.

Kaolin (phr)
2
4

Z6020 (%)
(MPa)
(%)
(MPa)
(%)
(KJ/m²)
(MPa)
(%)
(MPa)
(%)
(KJ/m²)

2
23
13
17
650
44
23
11
17
650
35

4
23
11
17
600
43
23
9
17
530
41

3.2.2. Composites Tensile Properties

Figures 4 and 5 depict the tensile characteristics variations for the composites prepared with unmodified kaolin and with kaolin treated with the alkylammonium salt. Thus, it appears from the Figure 4 that the yielding stress and strain values are slightly affected by kaolinite treatment and concentration.

Figure 4: PP composites yielding stress and strain variations as a function of treated and untreated kaolin concentration.

Figure 5: PP composites breaking stress and strain variations as a function of treated and untreated kaolin concentration.

The composites yielding behavior is essentially governed by the PP matrix due to the low rate of the incorporated mineral filler. However, it seems important to note that the values of the yielding strain of all the composites are higher than those of the matrix, probably because of the rigidity of the clay.

Figure 5 illustrates the variations of the stress and the strain at break as function of the filler rate for the composites with treated and untreated kaolin. The behavior at break of the composites has been markedly affected by the incorporation of the mineral filler. Thus, the strain noticeable decrease occurred from 600% for the nonfilled PP to a value of 60% for the composites with 5 phr of untreated kaolin and to 27% for that containing the same concentration of the filler treated with the alkylammonium salt. The decrease of the strain at break at this filler loading might be due to the decreased deformability at the interface the filler/matrix.

For the composites with 2 and 4 phr of kaolin treated with 2 and 4% of silane, the Table 2 shows that practically small variations of the tensile characteristics σ y, ε y, σ r, ε r are detected as a function of the kaolin and the coupling agent concentrations. Thus, it appears evident that these two low kaolin contents, even treated with the ammonium salt and the silane coupling agent cannot affect noticeably the matrix properties.

3.3. Melting and Crystallization Behaviors

Figures 6 and 7 compare the DSC cooling thermograms of neat PP with its various composites. In Figures 6(a), the effects of adding unmodified kaolin on the crystallization of PP are evident. The crystallization onset temperature and the crystallization peak temperature (temperature at the exotherm maximum) of PP, both shifted to lower temperatures as kaolin is added. The decrease in the crystallization temperature after introduction of the filler means that higher undercooling of the melt is necessary for the crystallization to occur [25]. We believe that the reason of this behaviour is the strong influence of the kaolinite on the chain dynamics. Although fillers usually act as nucleation centers [26], the crystallization in the present system is slowed down as a result of lower chain mobility.

(a)

(b)

Figure 6: DSC thermograms of (a) PP/untreated kaolin and (b) PP/treated kaolin cooled from the melt at 20°C/min.

(a)

(b)

Figure 7: DSC thermograms of PP composites containing (a) 2 phr and (b) 4 phr of kaolinite treated with 2% and 4% of silane, cooled from the melt at 20°C/min.

Figures 6(b) depicts the DSC cooling thermograms of neat PP and its ammonium modified kaolin composites. The crystallization retarding effect of the filler is still observed, but it is more obvious for the clay loadings of 4 and 5 phr, so the shifting of the crystallization temperature increases proportionally to the clay concentration. When comparing the thermograms of the composites including the three first modified kaolin loadings (1, 2, and 3 phr), with those of the composites containing the equivalent rates of the unmodified clay, we notice that the values of and are slightly lower to the matrix ones but sufficiently higher to those of the composites PP/unmodified kaolin. This observation indicates that the crystallization rate increases and the degree of supercooling required for the crystallization reduces when the modified clay is added. This fact can merely be linked to the treatment and to the interactions between the kaolinite modified surface and PP chains. Thus, the combined effect of the clay and of the interactions clay/matrix contributes to get an enhanced PP chains mobility and consequently a faster crystallization rate and higher crystallization temperatures, relatively to untreated kaolin composites. For the composites with 4 and 5 phr of kaolin, the effect of the clay loading is more prominent and the retarding effect is much more pronounced.

The crystallization behaviour of silane modified kaolinite composites exhibited the similar trend as above, as it is seen in Figures 7(a) and 7(b). In this case also, the surface treatment of the filler caused the variation of . The effect of the coupling agent concentration is unnoticeable. Additionally, the crystallization heat varied insignificantly for all the composites samples.

Figures 8(a) and 8(b) represent the DSC heating thermograms of neat PP and its composites heated from ambient temperature to 250°C at 10°C/min. The melting peak temperatures of the untreated and ammonium treated kaolin composites vary trivially with respect to that of neat PP. This result suggests that the addition of small kaolin concentrations and its treatment did not affect the structure and the stability of the formed PP crystals.

(a)

(b)

Figure 8: DSC heating thermograms of (a) PP/untreated kaolin and (b) PP/treated kaolin composites.

Similar melting peak results are observed in the case of the silane surface treated kaolin composites, as it is illustrated in Figures 9(a) and 9(b). So, from the observed thermograms, it seems that the surface treatment of the filler has a small effect on the melting temperature and on the crystallinity of the matrix.

(a)

(b)

Figure 9: DSC heating thermograms of PP composites containing (a) 2 phr and (b) 4 phr of kaolinite treated with 2% and 4% of silane.

These results indicate that the incorporation and the modification of the filler apparently affect the PP crystallization rate, but influence the PP crystallinity only slightly, as it is reported in the Table 3.

Table 3: PP/kaolin composites thermal characteristics determined from DSC scans.

Samples
(J/g)
(°C)
(J/g)
(°C)
(%)

Neat PP
63
144
68
106
41

PP/UK1
56
143
60
88
36

PP/UK2
65
142
65
90
39

PP/UK3
59
143
61
89
37

PP/UK4
54
143
65
90
39

PP/UK5
63
142
65
91
39

PP/TK1
60
143
67
106
40

PP/TK2
63
144
63
102
38

PP/TK3
57
144
58
102
35

PP/TK4
57
144
58
95
35

PP/TK5
59
143
65
93
39

PP/K2 2% Z6020
63
141
70
96
42

PP/K2 4% Z6020
65
142
67
94
40

PP/K4 2% Z6020
55
141
64
94
38

PP/K4 4% Z6020
59
142
66
94
40

3.4. Composites Thermal Stability

TGA was employed to evaluate thermal stabilities of the different formulated samples which degradation characteristics are reported in the Table 4. When considering the matrix and the composites with untreated kaolin, the main deductions can be summarized as follows. The used PP started to degrade around 250°C, and finishes at 393°C with approximately no residual mass. The PP/untreated kaolin composites showed almost an identical thermal stability and as the PP matrix, they are decomposed on only one stage. All the composites started degradation at 250°C, however; a noticeable increase is observed on the value of the temperature at which the degradation is achieved . For example, the composite including 5 phr of kaolin begins to degrade at 250°C and finished at 405°C, with a residual mass around 5.5%, which is approximately the clay loading in the composite. exhibit the same variations as because it increases when the kaolin concentration increases. Indeed, varies from 374°C for neat PP to 389°C for the formulation including 5 phr of kaolinite. These observations suggest that the addition of small amounts of the filler enhances noticeably the thermal stability of the whole material [27].

Table 4: PP/kaolin composites degradation characteristics determined from TGA scans.

Samples
(°C)
(°C)
(°C)

Neat PP
250
374
393

PP/UK1
250
380
395

PP/UK2
249
383
400

PP/UK3
252
386
404

PP/UK4
247
384
403

PP/UK5
250
389
405

PP/TK1
252
376
394

PP/TK2
250
370
398

PP/TK3
253
377
394

PP/TK4
250
387
403

PP/TK5
248
388
404

PP/K2 2% Z6020
245
382
397

PP/K2 4% Z6020
245
384
400

PP/K4 2% Z6020
245
387
400

PP/K4 4% Z6020
245
388
400

The thermal stability of the PP/modified kaolin composites, exhibited a similar trend as the above ones. All the formulations started degradation around 250°C and finishes with a residual mass equivalent to the clay loading in the composites. and showed an enhancement relative to the matrix, but no variations were noticed when compared to the composites with unmodified clay. So, the thermal stability enhancement is mainly due to the clay, and small effects were noticed after the modification with the ammonium salt and the silane coupling agent.

4. Conclusion

This article reports the results of an investigation on the effects of kaolin loading and treatments with an alkylammonium salt and a silane coupling agent, on the mechanical and thermal properties of polypropylene.

Infrared analysis results supported the occurrence of a partial delamination during dry milling of kaolin with urea and the bonding of alkylammonium to its groups. The X-rays diffraction confirmed that the 001 reflection of the clay was not affected by the treatment, which states that the interactions concerned essentially the superficial groups of kaolinite via an adsorption process.

The mechanical characterization showed the decrease of the PP/kaolin composites impact strength due to aggregates formation and to the poor adhesion between the filler surface and the matrix. In the opposite, small variations were observed on the tensile characteristics, except for the composites with 5 phr of kaolinite, for which a strong decrease of the strain at break was noticed.

The DSC results indicated that the addition of modified and unmodified kaolin causes small variations on the crystallinity and on the melting temperature of the matrix. However, noticeable variations are deduced on the crystallization temperature which is shifted to lower values when the filler is added. The crystallization inhibiting effect of the kaolin filler is essentially pointed out on the crystallization temperature without affecting considerably the degree of crystallinity of the matrix. Also, the TGA results confirmed a slight enhancement of the thermal stability of the composites relative to the neat matrix.

References

Y. Wang and J. J. Wang, “Shear yield behavior of calcium carbonate-filled polypropylene,” Polymer Engineering and Science, vol. 39, no. 1, pp. 190–198, 1999.

G. Guerrica-Echevarria, J. I. Eguiazabal, and J. Nazabal, “Influence of molding conditions and talc content on the properties of polypropylene composites,” European Polymer Journal, vol. 34, no. 8, pp. 1213–1219, 1998.

A. Usoki, M. Kato, A. Okada, and T. Kurauchi, “Synthesis of polypropylene-clay hybrid,” Journal of Applied Polymer Science, vol. 63, no. 1, pp. 137–139, 1997.

A. C. Chinellato, S. E. Vidotti, G. H. Hu, and L. A. Pessan, “An acrylic acid modified polypropylene as a compatibilizing agent for the intercalation/exfoliation of an organically modified montmorillonite in polypropylene,” Journal of Polymer Science B, vol. 46, no. 17, pp. 1811–1819, 2008.

H. H. Murray, “Traditional and new applications for kaolin, smectite, and palygorskite: a general overview,” Applied Clay Science, vol. 17, no. 5-6, pp. 207–221, 2000.

H. H. Murray, “Applied clay mineralogy today and tomorrow,” Clay Minerals, vol. 34, no. 1, pp. 39–49, 1999.

L. Cabedo, E. Giménez, J. M. Lagaron, R. Gavara, and J. J. Saura, “Development of EVOH-kaolinite nanocomposites,” Polymer, vol. 45, no. 15, pp. 5233–5238, 2004.

S. Olejnik, A. M. Posner, and J. P. Quirk, “The intercalation of polar organic compounds into kaolinite,” Clay Minerals, vol. 8, pp. 421–434, 1970.

Y. Komori, Y. Sugahara, and K. Kuroda, “Direct intercalation of poly(vinylpyrrolidone) into kaolinite by a refined guest displacement method,” Chemistry of Materials, vol. 11, no. 1, pp. 3–6, 1999.

W. N. Martens, R. L. Frost, J. Kristof, and E. Horvath, “Modification of kaolinite surfaces through intercalation with deuterated dimethylsulfoxide,” Journal of Physical Chemistry B, vol. 106, no. 16, pp. 4162–4171, 2002.

E. Horváth, J. Kristóf, R. L. Frost, E. Jakab, É. Makó, and V. Vágvölgyi, “Identification of superactive centers in thermally treated formamide-intercalated kaolinite,” Journal of Colloid and Interface Science, vol. 289, no. 1, pp. 132–138, 2005.

R. L. Frost, J. Kristof, E. Horvath, and J. T. Kloprogge, “Modification of kaolinite surfaces through intercalation with potassium acetate, II,” Journal of Colloid and Interface Science, vol. 214, no. 1, pp. 109–117, 1999.

J. C. Dai and J. T. Huang, “Surface modification of clays and clay-rubber composite,” Applied Clay Science, vol. 15, no. 1-2, pp. 51–65, 1999.

R. L. Ledoux and J. L. White, “Infrared studies of hydrogen bonding interaction between kaolinite surfaces and intercalated potassium acetate, hydrazine, formamide, and urea,” Journal of Colloid And Interface Science, vol. 21, no. 2, pp. 127–152, 1966.

R. L. Frost, J. Kristof, L. Rintoul, and J. T. Kloprogge, “Raman spectroscopy of urea and urea-intercalated kaolinites at 77 K,” Spectrochimica Acta A, vol. 56, no. 9, pp. 1681–1691, 2000.

R. L. Frost, T. H. Tran, and J. Kristof, “The structure of an intercalated ordered kaolinite - A Raman microscopy study,” Clay Minerals, vol. 32, no. 4, pp. 587–596, 1997.

E. Makó, J. Kristóf, E. Horváth, and V. Vágvölgyi, “Kaolinite-urea complexes obtained by mechanochemical and aqueous suspension techniques-A comparative study,” Journal of Colloid and Interface Science, vol. 330, no. 2, pp. 367–373, 2009.

F. C. Chiu, S. M. Lai, J. W. Chen, and P. H. Chu, “Combined effects of clay modifications and compatibilizers on the formation and physical properties of melt-mixed polypropylene/clay nanocomposites,” Journal of Polymer Science B, vol. 42, no. 22, pp. 4139–4150, 2004.

F. Bellucci, A. Terenzi, A. Leuteritz et al., “Intercalation degree in PP/organoclay nanocomposites: role of surfactant structure,” Polymers for Advanced Technologies, vol. 19, no. 6, pp. 547–555, 2008.

O. Monticelli, Z. Musina, A. Frache, F. Bellucci, G. Camino, and S. Russo, “Influence of compatibilizer degradation on formation and properties of PA6/organoclay nanocomposites,” Polymer Degradation and Stability, vol. 92, no. 3, pp. 370–378, 2007.

T. S. Ellis and J. S. D'Angelo, “Thermal and mechanical properties of a polypropylene nanocomposite,” Journal of Applied Polymer Science, vol. 90, no. 6, pp. 1639–1647, 2003.

S. Letaief, T. A. Elbokl, and C. Detellier, “Reactivity of ionic liquids with kaolinite: melt intersalation of ethyl pyridinium chloride in an urea-kaolinite pre-intercalate,” Journal of Colloid and Interface Science, vol. 302, no. 1, pp. 254–258, 2006.

B. Wunderlich, Macromolecular Physics, vol. 3, Academic Press, New York, NY, USA, 1980.

M. Valášková, M. Rieder, V. Matějka, P. Čapková, and A. Slíva, “Exfoliation/delamination of kaolinite by low-temperature washing of kaolinite-urea intercalates,” Applied Clay Science, vol. 35, no. 1-2, pp. 108–118, 2007.

A. S. Luyt, M. D. Dramićanin, Ž. Antić, and V. Djoković, “Morphology, mechanical and thermal properties of composites of polypropylene and nanostructured wollastonite filler,” Polymer Testing, vol. 28, no. 3, pp. 348–356, 2009.

J. Njuguna, K. Pielichowski, and S. Desai, “Nanofiller-reinforced polymer nanocomposites,” Polymers for Advanced Technologies, vol. 19, no. 8, pp. 947–959, 2008.

M. L. Lopez-Quintanilla, S. Sánchez-Valdés, L. F. R. de Valle, and F. J. Medellin-Rodriguez, “Effect of some compatibilizing agents on clay dispersion of polypropylene-clay nanocomposites,” Journal of Applied Polymer Science, vol. 100, no. 6, pp. 4748–4756, 2006.