Effect of Surface Modification of Palygorskite on the Properties of Polypropylene/Polypropylene-g-Maleic Anhydride/Palygorskite Nanocomposites.
Palygorskite (Pal) is a type of clay with a unique three-dimensional structure and fibrous morphology, exhibiting chemical and thermal stability, high aspect ratio, large specific surface area (150-200 m /g), and mechanical strength [1,2].
The chemical formula for palygorskite is reported as [(Mg, Al, Fe)5 [Si.sub.8][O.sub.20][(OH).sub.2][(O[H.sub.2]).sub.4] x M[H.sub.2]O ; the clay structure is composed of octahedral and tetrahedral units of silicates that form interconnected channels with dimensions of 3.7 x 10.6 [Angstrom]. Substitutions of Si for Al atoms in the tetrahedral units provide to clay a cation exchange capacity (CEC) ranging from 20 to 30 meq/100 g . These interesting properties suggest that Pal can be used as polymer nanofiller , although it is mainly employed as a catalyst carrier [5-7] or as adsorbent material [8, 9].
The hydrophilic nature of Pal could represent a challenge for the production of polymer/Pal nanocomposites. A recurrent procedure to promote Pal dispersion within the polymer is to modify its surface with organic modifiers in order to reduce the interactions among silicate fibers and to promote compatibility with the polymer matrix. Pal has been traditionally modified with a silane coupling agent [1, 10-13] to produce polymer/Pal nanocomposites based on epoxy resin , Nylon 6 [14-17], natural rubber , ethylene-vinyl acetate copolymers , or poly-aniline . However, the use of cationic surfactants to modify Pal has been less frequently reported [21-25].
On the other hand, PP is one of the most widely used polyolefins due to its low cost, low density, and extraordinary versatility in terms of applications and recycling . Several studies have been devoted to improving the mechanical [27-30] and thermal properties of PP  by incorporating mineral fillers (i.e., clay) in an effort to diversify the use of PP. The intrinsic nonpolar nature of PP makes it incompatible with clay fillers; the use of modified clays and compatibilizers (such as polypropylene grafted maleic anhydride [32-34]) is a common approach to produce PP/clay nanocomposites. A number of studies have focused on the preparation of PP/PP-g-MAH/Pal nanocomposites [35-38], but despite these efforts, the factors promoting the dispersion of Pal and improvement of the properties are not yet completely understood.
In this study, the effect of surface modification of Pal on nanofiller dispersion and the enhancement of properties was evaluated on polypropylene (PP) nanocomposites prepared by melt compounding using polypropylene grafted maleic anhydride (PP-g-MAH) as compatibilizer. Thus, a Pal mineral was purified and characterized and separately modified with a conventional silane coupling agent (3-Aminopropyl)trimethoxysilane (APTMS) and a cationic surfactant (hexadecyl tributyl phosphonium bromide, HDTBP) to produce Pals with different surface energies. To the best of our knowledge, there are no previous reports concerning Pal modification with HDTBP to produce polymer nanofiller. It was expected that surface modification promotes the deagglomeration of silicate fibers, thereby improving dispersion during melt compounding and enhancing some properties. Pal characterization involved Scanning Electron Microscopy (SEM) and Fourier Transform Infrared Spectroscopy (FTIR); Pal dispersion within PP was determined by SEM and TEM; the mechanical and thermal properties (Thermogravimetric Analysis, TGA and Differential Scanning Calorimetry (DSC)) of the resulting nanocomposites were also determined.
2.1. Materials. Palygorskite mineral was directly collected from a seam in Chapab, Mexico. Pal was purified with hydrochloric acid (J. T. Baker, 37% w/v). Ethylene glycol from Sigma-Aldrich was used to determine the surface energy of modified Pal. Isotactic PP (Valtec HP423M, melt flow index of 3.8g/10 min, Mw = 232,400 g/mole, and density of 0.9 g/[cm.sup.3]) was used as a matrix, and PP-g-MAH of Eastman G Polymers [TM] (Eastman G-3015, maleic anhydride 1.32 wt.%, acid number of 15 mg KOH/g, and Mw = 47,000 g/mole) was used as compatibilizer. (3-Aminopropyl)trimethoxysilane (APTMS 99% purity) from Sigma-Aldrich and hexadecyl tributyl phosphonium bromide [HDTBP.sup.+][Br.sup.-], 98% purity) from Alpha Aesar were used to modify the Pal surface.
2.2. Clay Purification. Pal mineral (100 g), as received, was dispersed mechanically with 3L of distilled water for 1h. Subsequently, the slurry was filtered through a 70 mesh sieve (0.224 [micro]m, standard ASTM E 11-70) and 100 mL of hydrochloric acid solution (1 N) was added to the Pal slurry and stirred mechanically for 1 h. Several cycles of washing/centrifuge were carried out until a pH ~7 was achieved . Finally, the purified Pal (Pal-1) was dried in a convection oven at 100[degrees]C for 24 h. A cation exchange capacity of 26.2 meq/100 g was determined for Pal, following the procedure reported in the literature .
2.3. Pal Modification with Silane Coupling Agent. Conventional silane modification was performed on Pal-1 : 10 g of Pal-1 was dispersed with 170 mL of toluene using an ultrasonic bath (10 min) and then it was filtered through a 70 mesh sieve. APTMS was added dropwise to the mixture (under vigorous mechanical stirring) at the ratio Pal : silane of 1 : 1 g : ml. The reaction was conducted under reflux for 2 h at 45[degrees]C under mechanical stirring. The resulting modified Pal was washed with toluene and anhydrous ethanol to remove unreacted silane coupling agent. Finally, the silane modified Pal (Pal-2) was dried in a convection oven at 100[degrees]C for 24 h, ground, and sieved (70 mesh).
2.4. Pal Modification with the Phosphonium Surfactant. To produce a new organo-Pal, 25 g of Pal was mechanically dispersed in 2.5 L of distilled water for 1 h and then was filtered through a 70 mesh sieve and sonicated for 30 min (ultrasonic tip Vibra Cell, model 750 VC, at 20 kHz). Subsequently, HDTBP solution was slowly added to the Pal suspension; the amount of surfactant corresponded to the 1.1 CEC of Pal. The reaction was then maintained under mechanical stirring at 80[degrees]C for 5 h . The modified Pal was washed several times with distilled water to remove the bromide ions. Finally, the modified Pal (Pal-3) was dried in a convection oven at 100[degrees]C for 24 h, ground, and sieved (70 mesh).
2.5. Preparation of PP/PP-g-MAH/Pal Nanocomposites. The dried Pals were melt-compounded separately with PP/PP-gMAH (containing 5 wt.% of PP-g-MAH) in a batch mixer Plasticorder, Brabender at 190[degrees]C for 5 min at 100 rpm to obtain PP/PP-g-MAH/Pal nanocomposites. Pal contents were 0.5, 1, and 2 wt.%. Other studies have reported that the tensile mechanical properties of PP did not increase considerably at concentrations higher than 2 wt.% of Pal [35, 37]. The composites were compression molded at 190[degrees]C in a lab press for 3 min at 45 kN clamping load; specimens for further characterization were obtained from the above plates (120 x 120 mm, 1 mm thick).
3.1. Scanning Electron Microscopy (SEM) and Transmission Electron Microscopy (TEM) Analysis. Pals and the fracture surfaces of PP/PP-g-MAH/Pal nanocomposites (under cryogenic conditions) were observed using a variable-pressure Scanning Electron Microscope Jeol model JSM-6360 LV (20 kV); samples were coated with a thin layer of gold. TEM analysis was carried out with a Titan 80-300 k microscope, on ultrathin samples obtained by a microtome under cryogenic conditions.
3.2. Fourier Transform Infrared Spectroscopy (FTIR). FTIR analysis was carried out on Pals with a FTIR Nicolet 8700. KBr/Pal tablets (2% wt. clay) were obtained using a KBr pellet die applying a 20 kN clamping load for 5 min. The scanning range was from 4000 to 400 cm 1 with a resolution of 4 [cm.sup.-1] ; the results are the average of 100 scans.
3.3. Thermogravimetric Analysis (TGA). The thermal stability of PP/PP-g-MAH/Pal nanocomposites was determined with a Thermogravimetric Analyzer TGA-7 Perkin Elmer, from 50[degrees]C to 700[degrees]C with a heating rate of 10[degrees]C/min under a Nitrogen atmosphere; the sample weight was 5 mg.
3.4. Contact Angle Measurements. To assess the change in the hydrophilicity of Pal, the contact angles of sessile drops of ethylene glycol (Sigma-Aldrich) on the surface of Pal tablets were measured at room temperature. Pal tablets were prepared by compressing 300 mg of Pal using a KBr pellet die applying 50 kN clamping force for 5 min (Lab Carver Press). The values of contact angles were determined using the dynamic sessile drop method with a goniometer-Rame-Hart Instrument Co model 250. The average contact angles were calculated from twenty measurements of four different drops.
3.5. Mechanical Tensile Properties. Mechanical tensile testing was carried out using a universal tensile machine (Mini SHIMADZU model AGS-1KN); specimens were deformed at 5mm/min at room temperature according to the standard test method ASTM-638D. Elastic modulus, tensile strength, and elongation at break were determined. The total length for the dog-bone specimen was 115 mm, gauge length was 25 mm, and the narrow section width was 6 mm.
3.6. Differential Scanning Calorimetry (DSC). DSC analysis was carried out using a Perkin Elmer DSC-7 calorimeter under a Nitrogen atmosphere. The samples (6mg) were sealed in aluminum pans and heated from 50[degrees]C to 250[degrees]C at 10[degrees]C/min and cooled at 50[degrees]C/min; two heating runs were conducted.
4. Results and Discussion
4.1. Morphology of Pals. The morphology of Pals was assessed by SEM micrographs (Figure 1). The morphology of Pal-1 is presented as a fibrillar structure (Figure 1(a)); the diameter ranges from 20 to 30 nm and the length shows a wide range from hundreds of nanometers to few microns. In addition, Pal was observed as agglomerates due to the strong interactions among individual silicate fibers . SEM micrographs of Pal-2 (Figure 1(b)) revealed no substantial changes in the clay fiber morphology after silane treatment. Clay aggregates seem to be more compact; it may be possible therefore that silane molecules can contribute to the aggregation among clay particles. Finally, Figure 1(c) shows Pal-3 fibers; some clay particles appear to be separated from the agglomerates, possibly due to the weakened clay-clay interactions after the surface modification. The SEM observations suggest that the experimental conditions used during surface modification of Pal did not significantly modify the aspect ratio morphology.
4.2. FT-IR Characterization. FT-IR analysis was conducted to verify the surface modification of Pal; the FT-IR spectra of Pal-1, Pal-2, and Pal-3 are presented in Figure 2. The band in 3615 [cm.sup.-1] for the Pal-1 spectrum can be attributed to the stretching vibrations of Mg-OH from the dioctahedral units. A band associated with the stretching vibrations of the coordinated water is observed at 3547 [cm.sup.-1] . The band at 3400 [cm.sup.-1] corresponds to the stretching vibrations of absorbed and zeolitic water. The band at 1650 [cm.sup.-1] was attributed to OH bending vibrations of coordinated, absorbed, and zeolite water ; it is probable that the above band could overlap the signal associated with vibrations of the amino groups from silane molecules at 1608 [cm.sup.-1]. The bands at 1194 [cm.sup.-1] and 1034 [cm.sup.-1] were attributed to asymmetric stretching vibrations from Si-O. The band in 987 [cm.sup.-1] is due to vibrations stretching perpendicularly to the plane of Si-O, and the band at 647 [cm.sup.-1] could be attributed to stretching vibrations from Mg bonded water (zeolitic and surface absorbed) . The signal in 509 [cm.sup.-1] corresponds to the deformation of Si-O bonds from tetrahedral sheets . The IR signals are consistent with the results reported in other studies.
The FT-IR spectrum for Pal-2 shows additional bands, for example, a band at 2930 [cm.sup.-1] corresponding to the stretching vibrations of C-H bonds from the silane molecule [43, 44]. Bands associated with the symmetric bending vibrations for N-H due to the amino groups of the silane grafted on the surface of Pal were observed at 1495 [cm.sup.-1] and 1390 [cm.sup.-1] . On the other hand, the bands at 2926 and 2855 [cm.sup.-1] in the FT-IR spectrum for Pal-3 correspond to the symmetric and antisymmetric stretching vibrations from -C[H.sub.2]- groups of surfactant, respectively [9, 20]. The band in 1470 [cm.sup.-1] corresponds to the deformation of C-H bonds  from the alkyl chains of surfactant. The experimental evidence suggests that the silane and cation surfactant molecules were successfully grafted to the Pal surface.
4.3. Contact Angle Measurements. Contact angle measurements have been reported for other mineral clays such as montmorillonite (MMT) [46-48], kaolinite , and smec-tite  for the purpose of verifying the surface modification of clays. Figure 3 shows profiles of the sessile droplets of ethylene glycol on the surfaces of Pal tablets. Ethylene glycol was chosen as test liquid due to its viscosity and polarity. The average values of the contact angle for the Pals are shown in Table 1, which tend to increase with the surface treatment. Pal-1 belongs to a type of natural hydrophilic silicate showing hydrophilic nature; as a consequence, the contact angle of a sessile droplet of a partial hydrophilic was small. The increment in the contact angle for other Pals can be interpreted as an increase in the hydrophobicity of the Pal surface due to the hydrophobic silane coupling agent or the cationic surfactant grafted to the surface. The enhancement of hydrophobicity in the organically modified clays could lead to an improvement in the dispersion/exfoliation of clay within the polymer .
4.4. Pal Dispersion within the PP/PP-g-MAH/Pal Nanocomposites. The dispersion of Pal within PP matrix was determined by SEM observations (Figure 4) of the fracture surfaces of PP/PP-g-MAH/Pal nanocomposites with three different types of Pal (2 wt.% Pal content). Figures 4(a)-4(c) correspond to Pal-1 nanocomposites at different magnifications, in which Pal-1 was distributed as aggregates in micrometer size; the light dots are the fractured ends of fibrous crystals of Pal. Figures 4(d)-4(f) correspond to PP/PP-g-MA/Pal-2 nanocomposites where Pal-2 was distributed as smaller agglomerates; the results suggest that Pal dispersion was improved with the surface treatment due to the weakening of interactions among palygorskite single crystals. Weaker interactions among fibers allow the separation of Pal crystals from the bundles during the melt compounding . Finally, Figures 4(g)-4(i) correspond to PP/PP-g-MA/Pal-3 nanocomposites. Interestingly, small aggregates were found on the fractured surface indicating good distribution and dispersion of Pal. The experimental evidence suggests that the surfactant modification of Pal effectively improved the compatibility among components, resulting in a uniform distribution and dispersion of Pal and inhibition of Pal reagglomeration.
TEM images of the PP/PP-g-MA/Pal nanocomposites at 2% w/w Pal content are shown in Figure 5. In Figures 5(a)-5(c), aggregates of Pal-1 with diameters around 193 nm are observed; the measurements were carried out using ImageJ software. On the other hand, in Figures 5(d)-5(f), the silicate fibers of Pal-2 are dispersed within the polymer matrix with aggregates with diameter around 144 nm. The Figure 5(g) shows the transversal view of Pal-3 fibers well dispersed within the PP/PP-g-MAH blend. Figures 5(h)-5(i) show details of the distribution and dispersion of Pal-3; the diameter of Pal-3 aggregate ranges from 20 to 40 nm. The results indicate that the distribution and dispersion of silicate fibers depend on the reduction of surface energy of Pal: Pal-3 modified with longer alkane molecules shows better dispersion and distribution.
4.5. Mechanical Properties. The tensile mechanical properties of PP/PP-g-MAH/Pal nanocomposites are shown in Figure 6. In general, Young's modulus (Figure 6(a)) increased with Pal concentration due to the stiffness of silicate fibers, depending on the surface modification of Pal. For instance, the modulus of PP/PP-g-MAH/Pal-1 nanocomposites increase rapidly with a Pal load at low concentration (0.5 and 1 wt.%), while, at higher Pal content, the modulus reaches a plateau. It may be that, at this relatively high concentration of Pal, the agglomeration of silicate fibers acts as a stress concentrator, as reported in other studies [35, 37].
However, the nanocomposites containing Pal-2 and Pal-3 exhibited higher values of Young's modulus compared with Pal-1 nanocomposites; the results suggest that the reduction of surface energy of silicate fibers promoted its dispersion and compatibility with the polymeric matrix, increasing the stiffness of nanocomposites at low concentration of Pals. There are no significant differences in the modulus with the experimental error for Pal-2 and Pal-3 nanocomposites.
On the other hand, the tensile strength of PP (Figure 6(b)) increased slightly with the addition of Pals; however, no significant differences were observed with the experimental error. It is important to point out that the strength of the polymer matrix was not only preserved but actually slightly improved; it has also been reported that the inclusion of mineral filler within PP tends to reduce the matrix strength . Further studies are required in order to promote the polymer-Pal interactions by increasing the content of PP-g-MAH to improve the mechanical properties.
It is widely accepted that the incorporation of nanoreinforcers in polymeric materials tends to reduce the elongation at break of nanocomposites. The experimental results concerning elongation at break (Figure 6(c)) indicate that the property decreases with the Pal content (regardless of the type of Pal used), possibly due to the restriction in molecular movement of the polymer chains between silicate fibers and/or Pal agglomeration [31, 53].
4.6. Thermal Properties. The TGA analysis provides relevant information concerning the thermal stability of the nanocomposites. The TGA traces in Figure 7 depict the variations of the residual mass as a function of temperature for pure PP, PP/PP-g-MAH, and PP/PP-g-MAH/Pal nanocomposites. TGA traces for PP and PP PP-g-MAH (Figure 7(a)) show that the thermal decomposition ofthe materials occurs in one step; PP/PP-g-MAH seems to be slightly less thermally stable than PP due to the lower molecular weight of the compatibilizer. TGA traces of Pal-1 nanocomposites were shifted at higher temperatures especially at 1 and 2% wt. of Pal-1. On the other hand, the TGA traces of nanocomposites containing Pal-2 showed a drastic shift toward higher temperatures with the inclusion of Pal-2 even at the lowest concentration of Pal-2 and thermal stability increased with filler concentration (Figure 7(b)). The thermal stability of PP/PP-g-MAH/Pal-3 nanocomposites (Figure 7(c)) presents an interesting behavior: the TGA traces were shifted to higher temperatures at low content of Pal-3 and the thermal stability remained, regardless of the Pal-3 content. The results suggest that the thermal stability of PP nanocomposites depended on the degree of Pal dispersion promoted by the surface modification, with the Pal modified with the phosphonium surfactant producing the best results. The improvement in the thermal stability of PP/clay nanocomposites is attributed to a barrier effect of the dispersed particles of the clay, which can minimize the permeability of the volatile degradation products from the nanocomposites [31, 53], as well as the higher thermal stability of clays modified with phosphonium surfactants [54, 55].
The effect of Pal dispersion on the crystallinity of PP was evaluated by DSC. Figure 8 shows the DSC traces (corresponding to the second heating run) for PP, PP/PP-g-MAH, and PP/PP-g-MAH/Pal nanocomposites as a function of type and concentration of Pal. PP exhibited a melting peak at 165.1[degrees]C and PP/PP-g-MAH at 165.8[degrees]C. In general, Pal nanocomposites exhibited the melting peak in the same temperature range. Table 2 depicts the melting point (Tm), melting enthalpy (AHC), and the degree of crystallinity (Xc). The degree of crystallinity was calculated considering the melting enthalpy for 100% crystalline PP to be 190.6 J/g . A slight shift of the melting temperatures of nanocomposites to lower temperatures was observed, which might be related to the reduction in the crystallite size due to the presence of palygorskite .
The degree of crystallinity of PP matrix from nanocomposites tends to increase with Pal content, regardless of the surface treatment. PP/PP-g-MAH/Pal-1 shows lower values in the degree of crystallinity given that the Pal agglomerates reduce the concentration of active sites for nucleation . Thus, the better dispersed Pal-2 and Pal-3 in nanocomposites act as effective nucleation agents, increasing slightly the degree of crystallinity.
The effect of surface modification of Pal on filler dispersion and the mechanical and thermal properties was evaluated. Natural palygorskite was purified and surface modified separately to produce a silane modified Pal and a new phosphonium surfactant modified Pal. PP/PP-g-MAH/Pal nanocomposites were melt-compounded with different concentration of Pals. FT-IR analysis confirmed the surface modification of Pal and the contact angle measurements suggested that hydrophilicity of Pal was slightly reduced with the surface modification.
Pal particles were dispersed in different manners depending on the surface treatment. Pristine Pal was poorly distributed/dispersed within PP; however, Pal dispersion was improved when the surface of Pal was modified with a silane coupling agent or cationic surfactant, and the latter was better dispersed. It is possible that the longer alkyl chains of the cationic surfactant promoted interactions among polymer chains and modified Pal, thereby improving the dispersion. Young's modulus increased and maximum strength slightly improved with Pal content, and elongation at the break tended to decrease. As expected, samples with improved dispersion of Pal exhibited relatively improved mechanical properties. On the other hand, the thermal stability of nanocomposites depended on the degree of Pal dispersion; contrarily, the crystallinity of the nanocomposites is affected slightly by Pal, at least under the conditions described in this study.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
The present study was financially supported by FOMIX-Yucatan Grant 6030200001 and the Conacyt-Mexico Grant no. 222908. The technical support from Rossana Vargas-Coronado and Santiago Duarte-Aranda on FTIR analysis and SEM observations is highly appreciated.
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David Cisneros-Rosado and Jorge Alonso Uribe-Calderon
Centro de Investigacion Cientifica de Yucatan, A.C., Unidad de Materiales, Calle 43 No. 130 x 32y 34, Colonia Chuburna de Hidalgo, 97205 Merida, YUC, Mexico
Correspondence should be addressed to Jorge Alonso Uribe-Calderon; email@example.com
Received 22 February 2017; Revised 12 May 2017; Accepted 4 June 2017; Published 19 July 2017
Academic Editor: Domenico Acierno
Caption: FIGURE 1: SEM micrographs for palygorskite samples: (a) Pal-1, (b) Pal- 2, and (c) Pal-3.
Caption: FIGURE 2: FT-IR spectra of Pal-1, Pal-2, and Pal-3.
Caption: FIGURE 3: Profiles of sessile drops of ethylene glycol on the surfaces of: (a) Pal-1, (b) Pal-2, and (c) Pal-3, respectively.
Caption: FIGURE 4: SEM micrographs of the fractured surface at different magnifications of PP/PP-g-MAH/Pal nanocomposites (2 wt.%): Pal-1 (a), (b), and (c); Pal-2 (d), (e), and (f); Pal-3 (g), (h), and (i).
Caption: FIGURE 5: TEM micrographs of PP/PP-g-MAH/Pal nanocomposites: Pal-1 ((a) to (c)), Pal-2 ((d) to (f)), and Pal-3 ((g) to (i)).
Caption: FIGURE 6: Mechanical properties of PP/PP-g-MAH/Pal nanocomposites: (a) Young's modulus, (b) maximum strength, and (c) elongation at the break.
Caption: FIGURE 7: TGA traces for PP and PP/PP-g-MAH/Pal nanocomposites (0.5, 1, and 2 wt.% Pal content): (a) Pal-1, (b) Pal-2, and (c) Pal-3.
Caption: FIGURE 8: DSC thermograms for PP, PP/PP-g-MAH, and PP/PP-g-MAH/Pal: (a) 0.5, (b) 1, and (c) 2 wt.% Pal content, respectively.
TABLE 1: Contact angles for ethylene glycol on three types of Pal. Sample [[theta].sub.0] ([degrees]) Purified-Pal 14.01 [+ or -] 0.99 APTMS-Pal 20.09 [+ or -] 2.27 HDTBP-Pal 23.04 [+ or -] 2.87 TABLE 2: DSC parameters for PP and PP/PP-g-MAH/Pal nanocomposites. Sample Tm ([degrees]C) PP 165.1 PP/PP-g-MAH 165.8 PP/PP-g-MAH/Pal-1 (0.5% w/w) 165.2 PP/PP-g-MAH/Pal-1 (1% w/w) 164.2 PP/PP-g-MAH/Pal-1 (2% w/w) 162.9 PP/PP-g-MAH/Pal-2 (0.5% w/w) 165.3 PP/PP-g-MAH/Pal-2 (1% w/w) 164.3 PP/PP-g-MAH/Pal-2 (2% w/w) 163.5 PP/PP-g-MAH/Pal-3 (0.5% w/w) 164.3 PP/PP-g-MAH/Pal-3 (1% w/w) 163.1 PP/PP-g-MAH/Pal-3 (2% w/w) 163.2 Sample [DELTA][H.sub.c] [X.sub.c] (J/g) (%) PP 79.7 41.8 PP/PP-g-MAH 79.9 42.7 PP/PP-g-MAH/Pal-1 (0.5% w/w) 79.3 41.8 PP/PP-g-MAH/Pal-1 (1% w/w) 80.4 42.4 PP/PP-g-MAH/Pal-1 (2% w/w) 79.8 41.9 PP/PP-g-MAH/Pal-2 (0.5% w/w) 80.2 42.5 PP/PP-g-MAH/Pal-2 (1% w/w) 80.6 42.7 PP/PP-g-MAH/Pal-2 (2% w/w) 81.4 43.6 PP/PP-g-MAH/Pal-3 (0.5% w/w) 82.6 44.2 PP/PP-g-MAH/Pal-3 (1% w/w) 80.9 42.7 PP/PP-g-MAH/Pal-3 (2% w/w) 83.6 44.8
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|Title Annotation:||Research Article|
|Author:||Cisneros-Rosado, David; Uribe-Calderon, Jorge Alonso|
|Publication:||International Journal of Polymer Science|
|Date:||Jan 1, 2017|
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