# The Use of Epoxy Silanes on Montmorillonite: An Effective Way to Improve Thermal and Rheological Properties of PLA/MMT Nanocomposites Obtained via “In Situ” Polymerization

Authors: Valentina Sabatini; Hermes Farina; Luca Basilissi; Giuseppe Di Silvestro; Marco A. Ortenzi
Journal: Journal of Nanomaterials
 (2015)

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## Abstract

Polylactic acid (PLA) nanocomposites were prepared via “in situ” ring opening polymerization (ROP) of lactide using a montmorillonite, Cloisite 15A, employed after surface treatment with 3-Glycidoxypropyltrimethoxysilane. The dispersion of the nanoparticles was checked using Wide Angle X-Ray Scattering (WAXS) and Transmission Electron Microscopy (TEM); both the effects of different amounts of montmorillonite and silane were measured on molecular weights and on thermal and rheological properties, using Size Exclusion Chromatography (SEC), Differential Scanning Calorimetry (DSC), thermogravimetric analyses (TGA), and rheological analyses. It was found that even very low amounts (0.1% w/w) of nanoparticles greatly affect nanocomposites properties. Unmodified montmorillonite tends to decrease molecular weights, deactivating the catalytic system used for ROP of lactide, but when epoxy silane is present molecular weights increase. Melt crystallization temperatures increase with modified nanoparticles, which enhance crystallization process. TGA analyses show that when pure montmorillonite is present, nanocomposites have lower thermal stability with respect to standard PLA; when silane is used thermal stability can get much higher than standard PLA as silane content increases. The rheological behaviour of nanocomposites shows that melt viscosity is far higher than that of standard PLA at low shear rates and also a marked shear thinning behaviour can be achieved.


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## Body

## 1. Introduction

Polylactic acid (PLA) is an aliphatic polyester derived from renewable resources [1], such as sweet corn or sugar beets. It can be synthesized either by direct condensation of lactic acid or by ring opening polymerization (ROP) of lactic acid cyclic dimer, lactide.PLA is receiving more and more attention both in scientific and in industrial research fields because it combines a low environmental impact, regarding both raw materials production and end-life disposal, with interesting features; some of them include reduction of CO2 emission in comparison to conventional petroleum-based commodity plastics [2], improvement of farm economies [3], good physical properties and processability [4], and biodegradation to lactic acid, which is not harmful for human body [5]. Moreover, when burned, it produces no nitrogen oxide gases and only one-third of the heat generated by polyolefins [6].In the last years, PLA has therefore dramatically increased its market share, especially for the production of packaging and disposables. Nevertheless the polymer still suffers from some drawbacks, preventing its use for even more applications; it has poor thermal and mechanical resistance in processing conditions [7] and poor gas barrier properties [8], which limit its applications as food packaging material, a field in which its use, despite a price higher than traditional polyolefins such as PE, PET, and PP, is justified when biodegradability is required [9].PLA nanocomposites have been investigated as possible solution to the problems evidenced, since they exhibit remarkably improved mechanical, thermal, and flexural properties, heat distortion temperature, and gas permeability compared to those of neat PLA polymers [10–13].When using minerals with nanoscale dimensions, two important aspects must be considered: the compatibility between polymer and minerals and their dispersion in the matrix. Many nanoparticles have a very high surface/volume ratio that favors the dispersion in the polymeric matrix; thus significant improvements of properties can be obtained even with low loadings of mineral, even up to 0.1% w/w, maintaining processing conditions similar to those of standard materials [14].Within this framework, in the last decades the addition of layered silicate nanoparticles, such as montmorillonite (MMT), to polymers has attracted great attention for the potentiality of these minerals to influence a number of properties: for example, polyamides layered silicate sheets exhibit, even at low filler content (1% w/w), marked improvements regarding mechanical, thermal, and barrier properties in comparison to the unfilled matrix and to more conventional composites [15].It is well known that there are two ideal types of nanostructures in polymer/MMT nanocomposites, deriving from intercalation and exfoliation [16, 17] of the mineral lamellae. The intercalated structure is formed when a few polymer molecules are inserted between MMT layers and the nanoparticles are therefore “packed.” On the other side, complete exfoliation is achieved when the macromolecules separate the lamellae and therefore mineral layers are individually dispersed in polymer matrix. Real morphologies of PLA/MMT nanocomposites rarely contain the two idealized nanostructures; these two structures often coexist in the nanocomposites, but it is believed that the remarkable mechanical and barrier properties of these materials result when exfoliation is dominant [18].Most of the scientific literature deals with PLA/MMT nanocomposites obtained via extrusion, using high torque twin-screw extruders to achieve an efficient dispersion of the mineral in the polymer matrix [19, 20] or via dissolution and reprecipitation [21]; there are only a few works about the “in situ” preparation of PLA/MMT nanocomposites [22, 23] that could result in being a very efficient way to have nanocomposites with high exfoliation degree thanks to the high residential time of the nanoparticles in the polymeric matrix and to the fact that, at the beginning of the polymerization, short macromolecular chains have high mobility and reduced dimensions, allowing them to better exfoliate the mineral lamellae.The present paper investigates the behaviour of PLA nanocomposites obtained using “in situ” polymerization; nanocomposites were prepared by bulk ring opening polymerization (ROP) of lactide using a MMT, trademark Cloisite 15A by Rockwood Additives Inc., modified with a quaternary ammonium salt between the lamellae, that increases the space between each layer promoting exfoliation [24]. Since another issue limiting exfoliation is the high difference of surface energy between the inorganic platelets of MMT and the organic polymeric matrix [25], in the present paper a silane, 3-Glycidoxypropyltrimethoxysilane, was used as coupling agent to modify the surface of MMT in order to have a higher compatibility with the organic matrix and therefore to enhance exfoliation during the polymerization. Surface modification with silanes is well known for traditional mineral fillers such as wollastonite, kaolin, or glass fiber; it has also been used with mineral nanoparticles [26] but it has been not intensively applied on nanoparticles used to create PLA nanocomposites. Just a few examples are present in literature, for example, regarding nanosilica [27], and show that silanes have a marked effect on many properties; the effects of surface modification of MMT were investigated on the molecular weight, thermal properties, and rheological behaviour of PLA/MMT nanocomposites prepared by ROP of lactide using different quantities of silane-modified MMT to understand if the presence of silane, together with the “in situ” synthesis, can lead to improvements in the properties of PLA/MMT nanocomposites in comparison to what is already present in literature.


## 2. Experimental

### 2.1. Materials and Methods

PLA was synthesized from LL-lactide PURASORB L (purity > 99.5%) purchased from Purac Biomaterials. Tin octanoate [Sn(oct)2], pyromellitic dianhydride (PMDA), methanol, chloroform, methylene chloride, and m-cresol were purchased from Sigma Aldrich Co. LLC. Cloisite 15A is a montmorillonite modified with an organic ammonium salt; it has an average packed diameter of 13 μm and ammonium salt concentration of 125 meq/100 g and was purchased from Rockwood Additives Inc. Key physical properties of this clay, as declared by the producer, are summarized in Table 1. In the text, it will be referred to as MMT. 3-Glycidoxypropyltrimethoxysilane (GF80) was purchased from Wacker Chemie AG. All the reagents were used without further purification.Table 1
Key physical properties of Cloisite 15A.
Modifier structure
Organomodifier
Density (g/mL)
d
001-spacing (nm)
Weight loss onignition (wt%)
Dimethyl dehydrogenated tallow ammonium
1.66
3.15
43


#### 2.1.1. Wide Angle X-Ray Scattering (WAXS)

Wide Angle X-Ray Scattering (WAXS) experiments were performed using a Rigaku DMAX-II diffractometer. Diffraction patterns were obtained in the range5°<2θ<60° with Cu-Kα radiation (λ=1.5405 Å) under the following conditions: 40 kV, 40 mA, step width 0.02°, time per step 2 sec, divergence slit 0.25°, Soller slit 0.04 rad, and antiscatter slit 0.5°. X-ray patterns are normalized on the main peak. The basal spacing of the clay was calculated using Bragg’s law (equation (1)), where n represents the integer of diffraction order, λ is the wavelength of the incident light (1.5405 Å), d is the lattice spacing, and θ is the angle of diffraction:(1)nλ=2dsin⁡θ.


#### 2.1.2. Transmission Electron Microscopy (TEM)

The dispersion of MMT in the polymeric matrix was evaluated via Transmission Electron Microscopy (TEM): samples were reduced into ultrathin sections of 80 nm by an Ultracut E microtome (Reichert), collected onto a 300-mesh copper grid and examined by an EFTEM Leo912ab TEM (Zeiss) operating at 80 kV. Digital images were acquired by Esivision CCD-BM/1K system.


#### 2.1.3. Size Exclusion Chromatography (SEC)

The effect of MMT on the molecular weight of the nanocomposites was evaluated using a SEC system having Waters 1515 Isocratic HPLC pump and a four Waters Styragel columns’ set (HR3-HR4-HR5-HR2) with a UV detector Waters 2487 Dualλ Absorbance Detector set at 230 nm using a flow rate of 1 mL/min and 60 μL as injection volume; samples were prepared dissolving 40 mg of polymer in 1 mL of anhydrous CH2Cl2; before the analysis, the solution was filtered with 0.45 μm filters. Given the relatively high loading, a check was performed using lower concentration of polymer (5 mg/mL), in order to verify that no column overloading could be observed. Anyway, higher loadings were preferred as UV signal of PLA is relatively weak.


#### 2.1.4. Differential Scanning Calorimetry (DSC)

DSC analyses were conducted using a Mettler Toledo DSC 1, on samples weighting from 5 to 10 mg each. Melting and crystallization temperatures were measured using the following temperature program:(i)
heating from 25°C to 200°C at 10°C/min;(ii)
5 min isotherm at 200°C;(iii)
cooling from 200°C to 25°C at 10°C/min;(iv)
2 min isotherm at 25°C;(v)
heating from 25°C to 200°C at 10°C/min.The first two cycles (heating and isotherm at 200°C) were conducted to eliminate residual internal stresses deriving from the synthesis. Glass transition temperature (Tg), specific heat (ΔCp), crystallization temperature (Tc), cold crystallization temperature (Tcc), melting temperature (Tm), crystallization enthalpy (ΔHc), cold crystallization enthalpy (ΔHcc), and melting enthalpy (ΔHm) were determined; a schematic DSC thermogram, reporting the transitions indicated, is shown in Figure 1.Figure 1
Schematic representation of calorimetric transitions in a DSC thermogram during heating and cooling cycles.Room temperature crystallinity (χc) attributable to cold crystallization of neat PLA and PLA nanocomposites was evaluated taking into account the amount of clay present in nanocomposites using the following equation [28]:(2)χc=ΔHcΔH°m∗1-%wt MMT/100∗100,where ΔHc is the specific crystallization enthalpy of the sample, ΔH°m is the melting enthalpy of the 100% crystalline polymeric matrix (93 J/g for PLA [29]), and %wt MMT is the weight percentage of MMT.


#### 2.1.5. Thermogravimetric Analyses (TGA)

TGA were performed using a TGA 4000 Perkin Elmer instrument; tests on the polymers have been conducted under nitrogen atmosphere on samples weighting from 5 to 10 mg with a program that provides single heating cycle from 30°C to 600°C at 10°C/min. The analyses of nanoparticles were conducted under nitrogen atmosphere heating from 30°C to 900°C at 10°C/min.


#### 2.1.6. Rheological Curves

Rheological analyses, conducted using frequency sweep experiments, were performed with a Physica MCR 300 rotational rheometer with a parallel plate geometry (ϕ=25 mm, distance between plates = 1 mm). Linear viscoelastic regimes of neat PLA and PLA nanocomposites were studied; strain was set equal to 5% and curves of complex viscosity as function of frequency were recorded, taking 30 points ranging from 100 Hz to 0.1 Hz with a logarithmic progression, at 190°C; in this paper shear rate but not angular frequency is reported on the x-axis.


### 2.2. Surface Modification of MMT

In order to improve the compatibility between the polymeric matrix and the inorganic surface of MMT, organosilane having epoxy functional groups, 3-Glycidoxypropyltrimethoxysilane (GF80), was used as coupling agent to modify the surface of the mineral.Reaction between silane and MMT is obtained via placing nanoparticles in a one-neck flask in methanol under magnetic stirring, using a MMT/methanol ratio of 1/10 w/w at room temperature; different amounts of silane are then introduced depending on the desired degree of modification. In this work three different quantities of silane, 2%, 7.5%, and 15% w/w on the nanoparticles, have been used. The addition is performed slowly, in about 30 minutes regardless of the quantity of silane, to avoid the formation of aggregates and to favour its good dispersion; the solution is kept under vigorous stirring for 12 hours at room temperature. The solvent is removed by evaporation under nitrogen flux and then the system is heated at 120°C under vacuum (about 4 mbar) for 2 hours. Nanoparticles are then chopped using a mortar to obtain a fine powder. An isothermal TGA at 70°C under nitrogen flow running for 180 minutes was performed to check the absence of residual solvent on the nanoparticles.


#### 2.2.1. Quantitative Determination of the Silane

The amount of GF80 effectively present on the MMT surface was determined by potentiometric titration of the tertiary amine deriving from the reaction between the epoxy groups and N,N′-dibutylamine. The GF80-modified MMT was dispersed in a solution of N,N′-dibutylamine in methylene chloride (1 gram of MMT was dispersed in a 50 mL solution of methylene chloride containing 1 gram of N,N′-dibutylamine); the dispersion was stirred at room temperature for 12 h and then the solvent and the free amine were evaporated under vacuum at 40°C for 1 hour. MMT was then dispersed in hot m-cresol and titrated with HCl 0.01 N in methanol. In Table2 the amount of silane measured via potentiometric titration of the terminal groups is shown.Table 2
Amount of silane present on Cloisite 15A surface determined via titration.
Silane added (w/w % on MMT)
meq/kg
2.0% GF80
119
7.5% GF80
380
15.0% GF80
712


### 2.3. Synthesis of PLA and PLA/MMT Nanocomposites

PLA and PLA/MMT nanocomposites were synthesized from LL-lactide in bulk according to the following procedure; LL-lactide (50 g) and tin octanoate (0.3% w/w on lactide −0.15 g; for PLA13: 3% w/w on lactide −1.5 g) added as catalyst were introduced in a 250 mL three-neck flask. Slow nitrogen flow was used to ensure the presence of inert atmosphere during the polymerization; mechanical stirring was provided (100 rpm). For the synthesis of nanocomposite PLAs, different quantities of MMT, namely, 1.0% w/w (0.5 grams) −0.5% w/w (0.25 grams) −0.1% w/w (0.05 grams), for PLA13 5% w/w (2.5 grams), on lactide, were introduced in the feed together with the other reagents. Reactions were conducted in a closed oven at 180°C for 2 hours, using mechanical stirring (150 rpm). At the end of the reaction, the polymer was left in the flask under nitrogen flow and slowly cooled at room temperature; a solid polymer was obtained. PLA nanocomposites containing PMDA were synthesized using the same experimental method and conditions described before adding 0.1% w/w MMT (0.05 g) and PMDA in the feed (3.56∗10-5 mol -7.77∗10-3 g), together with the other reagents. After the syntheses, all samples underwent Solid State Polymerization (SSP) at 150°C for 12 hours under vacuum (about 4 mbar); all the analyses were conducted on the samples obtained after SSP.


### 2.4. Film Casting

Films for WAXS analyses were obtained from a chloroform solution; 10 grams of polymer was dissolved in 50 grams of CHCl3. The solution was cast on a glass surface and the solvent was evaporated at room temperature and pressure overnight. The absence of residual solvent in the films was checked via isothermal TGA (2 hours at 80°C under nitrogen flow). Film thickness was evaluated by Nikon eclipse ME600 optical microscope with Nikon digital camera light DS-Fi1, software Nis-Elements BR, and magnification 50x, and it was in the range 60–90 μm.


## 2.1. Materials and Methods

PLA was synthesized from LL-lactide PURASORB L (purity > 99.5%) purchased from Purac Biomaterials. Tin octanoate [Sn(oct)2], pyromellitic dianhydride (PMDA), methanol, chloroform, methylene chloride, and m-cresol were purchased from Sigma Aldrich Co. LLC. Cloisite 15A is a montmorillonite modified with an organic ammonium salt; it has an average packed diameter of 13 μm and ammonium salt concentration of 125 meq/100 g and was purchased from Rockwood Additives Inc. Key physical properties of this clay, as declared by the producer, are summarized in Table 1. In the text, it will be referred to as MMT. 3-Glycidoxypropyltrimethoxysilane (GF80) was purchased from Wacker Chemie AG. All the reagents were used without further purification.Table 1
Key physical properties of Cloisite 15A.
Modifier structure
Organomodifier
Density (g/mL)
d
001-spacing (nm)
Weight loss onignition (wt%)
Dimethyl dehydrogenated tallow ammonium
1.66
3.15
43


### 2.1.1. Wide Angle X-Ray Scattering (WAXS)

Wide Angle X-Ray Scattering (WAXS) experiments were performed using a Rigaku DMAX-II diffractometer. Diffraction patterns were obtained in the range5°<2θ<60° with Cu-Kα radiation (λ=1.5405 Å) under the following conditions: 40 kV, 40 mA, step width 0.02°, time per step 2 sec, divergence slit 0.25°, Soller slit 0.04 rad, and antiscatter slit 0.5°. X-ray patterns are normalized on the main peak. The basal spacing of the clay was calculated using Bragg’s law (equation (1)), where n represents the integer of diffraction order, λ is the wavelength of the incident light (1.5405 Å), d is the lattice spacing, and θ is the angle of diffraction:(1)nλ=2dsin⁡θ.


### 2.1.2. Transmission Electron Microscopy (TEM)

The dispersion of MMT in the polymeric matrix was evaluated via Transmission Electron Microscopy (TEM): samples were reduced into ultrathin sections of 80 nm by an Ultracut E microtome (Reichert), collected onto a 300-mesh copper grid and examined by an EFTEM Leo912ab TEM (Zeiss) operating at 80 kV. Digital images were acquired by Esivision CCD-BM/1K system.


### 2.1.3. Size Exclusion Chromatography (SEC)

The effect of MMT on the molecular weight of the nanocomposites was evaluated using a SEC system having Waters 1515 Isocratic HPLC pump and a four Waters Styragel columns’ set (HR3-HR4-HR5-HR2) with a UV detector Waters 2487 Dualλ Absorbance Detector set at 230 nm using a flow rate of 1 mL/min and 60 μL as injection volume; samples were prepared dissolving 40 mg of polymer in 1 mL of anhydrous CH2Cl2; before the analysis, the solution was filtered with 0.45 μm filters. Given the relatively high loading, a check was performed using lower concentration of polymer (5 mg/mL), in order to verify that no column overloading could be observed. Anyway, higher loadings were preferred as UV signal of PLA is relatively weak.


### 2.1.4. Differential Scanning Calorimetry (DSC)

DSC analyses were conducted using a Mettler Toledo DSC 1, on samples weighting from 5 to 10 mg each. Melting and crystallization temperatures were measured using the following temperature program:(i)
heating from 25°C to 200°C at 10°C/min;(ii)
5 min isotherm at 200°C;(iii)
cooling from 200°C to 25°C at 10°C/min;(iv)
2 min isotherm at 25°C;(v)
heating from 25°C to 200°C at 10°C/min.The first two cycles (heating and isotherm at 200°C) were conducted to eliminate residual internal stresses deriving from the synthesis. Glass transition temperature (Tg), specific heat (ΔCp), crystallization temperature (Tc), cold crystallization temperature (Tcc), melting temperature (Tm), crystallization enthalpy (ΔHc), cold crystallization enthalpy (ΔHcc), and melting enthalpy (ΔHm) were determined; a schematic DSC thermogram, reporting the transitions indicated, is shown in Figure 1.Figure 1
Schematic representation of calorimetric transitions in a DSC thermogram during heating and cooling cycles.Room temperature crystallinity (χc) attributable to cold crystallization of neat PLA and PLA nanocomposites was evaluated taking into account the amount of clay present in nanocomposites using the following equation [28]:(2)χc=ΔHcΔH°m∗1-%wt MMT/100∗100,where ΔHc is the specific crystallization enthalpy of the sample, ΔH°m is the melting enthalpy of the 100% crystalline polymeric matrix (93 J/g for PLA [29]), and %wt MMT is the weight percentage of MMT.


### 2.1.5. Thermogravimetric Analyses (TGA)

TGA were performed using a TGA 4000 Perkin Elmer instrument; tests on the polymers have been conducted under nitrogen atmosphere on samples weighting from 5 to 10 mg with a program that provides single heating cycle from 30°C to 600°C at 10°C/min. The analyses of nanoparticles were conducted under nitrogen atmosphere heating from 30°C to 900°C at 10°C/min.


### 2.1.6. Rheological Curves

Rheological analyses, conducted using frequency sweep experiments, were performed with a Physica MCR 300 rotational rheometer with a parallel plate geometry (ϕ=25 mm, distance between plates = 1 mm). Linear viscoelastic regimes of neat PLA and PLA nanocomposites were studied; strain was set equal to 5% and curves of complex viscosity as function of frequency were recorded, taking 30 points ranging from 100 Hz to 0.1 Hz with a logarithmic progression, at 190°C; in this paper shear rate but not angular frequency is reported on the x-axis.


## 2.1.1. Wide Angle X-Ray Scattering (WAXS)

Wide Angle X-Ray Scattering (WAXS) experiments were performed using a Rigaku DMAX-II diffractometer. Diffraction patterns were obtained in the range5°<2θ<60° with Cu-Kα radiation (λ=1.5405 Å) under the following conditions: 40 kV, 40 mA, step width 0.02°, time per step 2 sec, divergence slit 0.25°, Soller slit 0.04 rad, and antiscatter slit 0.5°. X-ray patterns are normalized on the main peak. The basal spacing of the clay was calculated using Bragg’s law (equation (1)), where n represents the integer of diffraction order, λ is the wavelength of the incident light (1.5405 Å), d is the lattice spacing, and θ is the angle of diffraction:(1)nλ=2dsin⁡θ.


## 2.1.2. Transmission Electron Microscopy (TEM)

The dispersion of MMT in the polymeric matrix was evaluated via Transmission Electron Microscopy (TEM): samples were reduced into ultrathin sections of 80 nm by an Ultracut E microtome (Reichert), collected onto a 300-mesh copper grid and examined by an EFTEM Leo912ab TEM (Zeiss) operating at 80 kV. Digital images were acquired by Esivision CCD-BM/1K system.


## 2.1.3. Size Exclusion Chromatography (SEC)

The effect of MMT on the molecular weight of the nanocomposites was evaluated using a SEC system having Waters 1515 Isocratic HPLC pump and a four Waters Styragel columns’ set (HR3-HR4-HR5-HR2) with a UV detector Waters 2487 Dualλ Absorbance Detector set at 230 nm using a flow rate of 1 mL/min and 60 μL as injection volume; samples were prepared dissolving 40 mg of polymer in 1 mL of anhydrous CH2Cl2; before the analysis, the solution was filtered with 0.45 μm filters. Given the relatively high loading, a check was performed using lower concentration of polymer (5 mg/mL), in order to verify that no column overloading could be observed. Anyway, higher loadings were preferred as UV signal of PLA is relatively weak.


## 2.1.4. Differential Scanning Calorimetry (DSC)

DSC analyses were conducted using a Mettler Toledo DSC 1, on samples weighting from 5 to 10 mg each. Melting and crystallization temperatures were measured using the following temperature program:(i)
heating from 25°C to 200°C at 10°C/min;(ii)
5 min isotherm at 200°C;(iii)
cooling from 200°C to 25°C at 10°C/min;(iv)
2 min isotherm at 25°C;(v)
heating from 25°C to 200°C at 10°C/min.The first two cycles (heating and isotherm at 200°C) were conducted to eliminate residual internal stresses deriving from the synthesis. Glass transition temperature (Tg), specific heat (ΔCp), crystallization temperature (Tc), cold crystallization temperature (Tcc), melting temperature (Tm), crystallization enthalpy (ΔHc), cold crystallization enthalpy (ΔHcc), and melting enthalpy (ΔHm) were determined; a schematic DSC thermogram, reporting the transitions indicated, is shown in Figure 1.Figure 1
Schematic representation of calorimetric transitions in a DSC thermogram during heating and cooling cycles.Room temperature crystallinity (χc) attributable to cold crystallization of neat PLA and PLA nanocomposites was evaluated taking into account the amount of clay present in nanocomposites using the following equation [28]:(2)χc=ΔHcΔH°m∗1-%wt MMT/100∗100,where ΔHc is the specific crystallization enthalpy of the sample, ΔH°m is the melting enthalpy of the 100% crystalline polymeric matrix (93 J/g for PLA [29]), and %wt MMT is the weight percentage of MMT.


## 2.1.5. Thermogravimetric Analyses (TGA)

TGA were performed using a TGA 4000 Perkin Elmer instrument; tests on the polymers have been conducted under nitrogen atmosphere on samples weighting from 5 to 10 mg with a program that provides single heating cycle from 30°C to 600°C at 10°C/min. The analyses of nanoparticles were conducted under nitrogen atmosphere heating from 30°C to 900°C at 10°C/min.


## 2.1.6. Rheological Curves

Rheological analyses, conducted using frequency sweep experiments, were performed with a Physica MCR 300 rotational rheometer with a parallel plate geometry (ϕ=25 mm, distance between plates = 1 mm). Linear viscoelastic regimes of neat PLA and PLA nanocomposites were studied; strain was set equal to 5% and curves of complex viscosity as function of frequency were recorded, taking 30 points ranging from 100 Hz to 0.1 Hz with a logarithmic progression, at 190°C; in this paper shear rate but not angular frequency is reported on the x-axis.


## 2.2. Surface Modification of MMT

In order to improve the compatibility between the polymeric matrix and the inorganic surface of MMT, organosilane having epoxy functional groups, 3-Glycidoxypropyltrimethoxysilane (GF80), was used as coupling agent to modify the surface of the mineral.Reaction between silane and MMT is obtained via placing nanoparticles in a one-neck flask in methanol under magnetic stirring, using a MMT/methanol ratio of 1/10 w/w at room temperature; different amounts of silane are then introduced depending on the desired degree of modification. In this work three different quantities of silane, 2%, 7.5%, and 15% w/w on the nanoparticles, have been used. The addition is performed slowly, in about 30 minutes regardless of the quantity of silane, to avoid the formation of aggregates and to favour its good dispersion; the solution is kept under vigorous stirring for 12 hours at room temperature. The solvent is removed by evaporation under nitrogen flux and then the system is heated at 120°C under vacuum (about 4 mbar) for 2 hours. Nanoparticles are then chopped using a mortar to obtain a fine powder. An isothermal TGA at 70°C under nitrogen flow running for 180 minutes was performed to check the absence of residual solvent on the nanoparticles.


### 2.2.1. Quantitative Determination of the Silane

The amount of GF80 effectively present on the MMT surface was determined by potentiometric titration of the tertiary amine deriving from the reaction between the epoxy groups and N,N′-dibutylamine. The GF80-modified MMT was dispersed in a solution of N,N′-dibutylamine in methylene chloride (1 gram of MMT was dispersed in a 50 mL solution of methylene chloride containing 1 gram of N,N′-dibutylamine); the dispersion was stirred at room temperature for 12 h and then the solvent and the free amine were evaporated under vacuum at 40°C for 1 hour. MMT was then dispersed in hot m-cresol and titrated with HCl 0.01 N in methanol. In Table2 the amount of silane measured via potentiometric titration of the terminal groups is shown.Table 2
Amount of silane present on Cloisite 15A surface determined via titration.
Silane added (w/w % on MMT)
meq/kg
2.0% GF80
119
7.5% GF80
380
15.0% GF80
712


## 2.2.1. Quantitative Determination of the Silane

The amount of GF80 effectively present on the MMT surface was determined by potentiometric titration of the tertiary amine deriving from the reaction between the epoxy groups and N,N′-dibutylamine. The GF80-modified MMT was dispersed in a solution of N,N′-dibutylamine in methylene chloride (1 gram of MMT was dispersed in a 50 mL solution of methylene chloride containing 1 gram of N,N′-dibutylamine); the dispersion was stirred at room temperature for 12 h and then the solvent and the free amine were evaporated under vacuum at 40°C for 1 hour. MMT was then dispersed in hot m-cresol and titrated with HCl 0.01 N in methanol. In Table2 the amount of silane measured via potentiometric titration of the terminal groups is shown.Table 2
Amount of silane present on Cloisite 15A surface determined via titration.
Silane added (w/w % on MMT)
meq/kg
2.0% GF80
119
7.5% GF80
380
15.0% GF80
712


## 2.3. Synthesis of PLA and PLA/MMT Nanocomposites

PLA and PLA/MMT nanocomposites were synthesized from LL-lactide in bulk according to the following procedure; LL-lactide (50 g) and tin octanoate (0.3% w/w on lactide −0.15 g; for PLA13: 3% w/w on lactide −1.5 g) added as catalyst were introduced in a 250 mL three-neck flask. Slow nitrogen flow was used to ensure the presence of inert atmosphere during the polymerization; mechanical stirring was provided (100 rpm). For the synthesis of nanocomposite PLAs, different quantities of MMT, namely, 1.0% w/w (0.5 grams) −0.5% w/w (0.25 grams) −0.1% w/w (0.05 grams), for PLA13 5% w/w (2.5 grams), on lactide, were introduced in the feed together with the other reagents. Reactions were conducted in a closed oven at 180°C for 2 hours, using mechanical stirring (150 rpm). At the end of the reaction, the polymer was left in the flask under nitrogen flow and slowly cooled at room temperature; a solid polymer was obtained. PLA nanocomposites containing PMDA were synthesized using the same experimental method and conditions described before adding 0.1% w/w MMT (0.05 g) and PMDA in the feed (3.56∗10-5 mol -7.77∗10-3 g), together with the other reagents. After the syntheses, all samples underwent Solid State Polymerization (SSP) at 150°C for 12 hours under vacuum (about 4 mbar); all the analyses were conducted on the samples obtained after SSP.


## 2.4. Film Casting

Films for WAXS analyses were obtained from a chloroform solution; 10 grams of polymer was dissolved in 50 grams of CHCl3. The solution was cast on a glass surface and the solvent was evaporated at room temperature and pressure overnight. The absence of residual solvent in the films was checked via isothermal TGA (2 hours at 80°C under nitrogen flow). Film thickness was evaluated by Nikon eclipse ME600 optical microscope with Nikon digital camera light DS-Fi1, software Nis-Elements BR, and magnification 50x, and it was in the range 60–90 μm.


## 3. Results and Discussion

A list of the samples synthesized, where STD is a standard PLA, is provided in Table3.Table 3
List of samples synthesized.
Sample
GF80 (% w/w on MMT)
MMT(% w/w on lactide)
Tin octanoate(% w/w on lactide)
PMDA (g)
STD
—
—
0.3
—
PLA1
—
1
0.3
—
PLA2
—
0.5
0.3
—
PLA3
—
0.1
0.3
—
PLA4
2
1
0.3
—
PLA5
2
0.5
0.3
—
PLA6
2
0.1
0.3
—
PLA7
7.5
1
0.3
—
PLA8
7.5
0.5
0.3
—
PLA9
7.5
0.1
0.3
—
PLA10
15
1
0.3
—
PLA11
15
0.5
0.3
—
PLA12
15
0.1
0.3
—
PLA13
—
5
3
—
PLA14
—
0.1
0.3
7.77∗ 10−3
PLA15
15
0.1
0.3
7.77∗ 10−3


### 3.1. WAXS Analyses

Crystalline peaks of MMT powder with different amounts of GF80 (2%–7.5%–15%) were studied in order to understand if silane contributes to increasing the interlayer space between the lamellae. Neat MMT exhibits four main diffraction peaks: the major one at2θ=19.77° and three minor ones at 7.19°, 35.31°, and 54.24°, attributed to the reflections of the four crystal planes of MMT. When silane is present, all the four peaks are still visible (Table 4) and each of them has the tendency to shift to lower angles in comparison to pure MMT, as Figure 2 evidences (only peak 2 is almost unaffected), promoting exfoliation.Table 4
2θ values of neat MMT and modified MMT.
Diffraction peak
Neat MMT2θ  [°]
MMT − 2%w/w GF802θ  [°]
MMT − 7.5%w/w GF802θ  [°]
MMT − 15%w/w GF802θ  [°]
1
7.19
6.87
6.87
6.47
2
19.77
19.73
19.79
19.76
3
35.31
35.06
35.12
34.86
4
54.24
53.85
54.12
53.98Figure 2
WAXS diffractograms of unmodified MMT (red), MMT with 2% w/w GF80 (blue), MMT with 7.5% w/w GF80 (green), and MMT with 15% w/w GF80 (violet).According to Bragg’s law (equation (1)), lower 2θ indicates an increase in the distance of the diffraction planes, that is, an increase in the basal spacing. Neat MMT presents a single basal peak at 7.19° (2θ), corresponding to a d001-spacing of 12.28 Å, which is the basal space distance of the natural clay [30]. The patterns of MMT samples modified with different amounts of silane show basal reflections at 6.87° (d001-spacing = 12.86 Å) in the case of MMT − 2% and MMT − 7.5% and at 6.47° (d001-spacing = 13.65 Å) for MMT − 15%, indicating an increase in the distance of the diffraction planes of 0.58 Å and 1.37 Å, respectively. This phenomenon reveals that some intergallery expansion has taken place thanks to the presence of silane and the fact that the higher the quantity of silane the higher the spacing between lamellae.WAXS analyses were used also to determine the crystalline structure of nanocomposite PLAs: the analysis was performed on the films obtained from casting as described in Section2.1. WAXS patterns of MMT, of STD PLA, and of PLA containing 1.0% w/w and 0.1% w/w of unmodified MMT (PLA1 and PLA3, resp.), collected in the range of 2θ = 5–60°, are presented in Figure 3. In PLA1 and PLA3 a diffraction peak is present, at 2θ = 16.82° and 16.94°, respectively, consistent with the major crystalline peak of highly crystalline PLA [31].Figure 3
WAXS diffractograms of Cloisite 15A powder, STD PLA, PLA1, and PLA3.It is possible to observe an increase of the height of the diffraction peak as the amount of MMT increases. This behavior indicates that MMT promotes heteronucleation process.Figure4 shows WAXS patterns of STD PLA and of PLA with 1% w/w of modified MMT with 2% w/w of GF80 (PLA4) and with 15% w/w of GF80 (PLA10). The nanocomposites patterns show that diffraction peaks of PLA4 and PLA10 are higher than STD; this behavior indicates that modified MMT promotes the intercalation of MMT in PLA chains.Figure 4
WAXS diffractograms of STD PLA, PLA4, and PLA10.


### 3.2. TEM Images

Figure5 reports TEM images of PLA nanocomposites; in PLA1, unmodified MMT is dispersed in the polymeric matrix, with aggregates having big dimensions indicating that the mineral has not been efficiently exfoliated. A good exfoliation should result in a good dispersion of MMT platelets within the polymeric matrix, each platelet having a length of about 100–200 nm, a similar width, and a thickness of some nanometers [32, 33]. In Figure 5, the effect of silane is visible: as its quantity increases, the dispersion of MMT platelets is enhanced. In PLA1 an aggregate is shown having big dimensions (maximum length = 1.6 μm, width 500 nm): similar aggregates are scattered through the nanocomposite. In PLA4, aggregates are present together with better exfoliated platelets: the bigger aggregate (number 1) has a length of about 1 μm and width of about 500 nm. Other big aggregates (number 2) are about 500 nm × 100 nm or less: other particles have an average length of 154±100 nm and an average width of 41±25 nm (calculated on 20 particles). In PLA7 aggregates with lower dimension are visible, with the bigger one (number 1) being about 500 nm × 130 nm: average length is 122±55 nm and width is 38±18 nm. In PLA4 and PLA7 the presence of some aggregates influences the dispersity of data collected. In Supporting Information, images of PLA4 (seeS1in Supplementary Material available online at http://dx.doi.org/10.1155/2015/418418) and PLA7 (S2) with lower magnification are presented. In PLA10, MMT is homogeneously dispersed and no big aggregates are visible: average length is 110±40 nm; average width is 33±15 nm.Figure 5
TEM images 1% w/w of PLA1 (a), PLA7 (b), PLA4 (c), and PLA10 (d).
(a)
(b)
(c)
(d)


### 3.3. Size Exclusion Chromatography (SEC)

Numeral average molecular weights (Mn-) and molecular weight distribution (D) determined via SEC and expressed as polystyrene equivalents are provided in Table 5; as described in Section 2.1, samples were filtered with a 0.45 μm filter; therefore molecular weight data refer only to the polymer present in the solution.Table 5
SEC data of PLAs synthesized.
Sample
M
n
-
D
STD
54124
1.79
PLA1
29901
1.26
PLA2
28563
1.33
PLA3
33238
1.29
PLA4
59230
1.86
PLA5
57431
1.85
PLA6
53611
1.80
PLA7
61551
1.88
PLA8
62045
1.89
PLA9
62117
1.89
PLA10
59683
1.88
PLA11
58661
1.87
PLA12
59342
1.89
PLA13
53991
1.77Samples PLA1, PLA2, and PLA3, containing unmodified MMT, show that the presence of pure MMT interferes with the polymerization process, lowering the molecular weights as the quantity of mineral increases. Two possible explanations for this phenomenon can be given. The first one is related to the fact that –OH groups on the surface of unmodified MMT can potentially initiate the polymerization, as already reported in literature [34]. Since molecular weight distribution values of PLA1, PLA2, and PLA3 are much lower than that of STD, a second possible explanation, alternative to the first one, is related to the fact that the free acidic sites of unmodified MMT may slow the kinetics of polymerization process partially deactivating the catalyst. The lower activity of catalyst decreases the kinetics of ROP but also the kinetics of transesterification reaction that is the cause of polydispersity increase.PLA13, containing a very high quantity of catalyst (3% w/w) and of MMT (5% w/w), was synthesised to confirm the validity of one of these hypotheses: SEC analysis shows thatMn- and D of PLA13 are very close to those of STD sample (Mn-: 53991; D: 1.77). These values demonstrate that pure MMT has the tendency to deactivate part of the catalyst, since higher amounts of tin octanoate lead to a PLA with high molecular weight; the second hypothesis is therefore confirmed.Nanocomposites containing silane-modified MMT haveMn- comparable with that of pure PLAs even when only 2% w/w of silane is used. Molecular weights tend to increase as the quantity of silane increases, indicating that epoxy silane reacting with MMT –OH surface groups decreases the interaction of MMT with catalyst.Since SEC refers only to the polymer that is present in solution, two samples were synthesized to confirm the reaction between epoxy silane and end groups of the growing polymeric chain: one using the same feed and conditions of PLA3 (named PLA14) and one using the same feed and conditions of PLA12 (named PLA15); in both PLA14 and PLA15 a tetrafunctional comonomer, pyromellitic dianhydride (PMDA,3.56∗10-5 mol in 50 g of lactide), was added in the feed. In PLA15, 0.1% w/w on lactide of MMT having 712 meq/kg of silane (i.e., 712 meq/kg of epoxy groups, see Table 1) is introduced in the feed. This means that the concentration of epoxy groups deriving from silane-modified MMT is 0.712 meq/kg of lactide (i.e., 3.56∗10-5 mol in 50 g of lactide). The concentration of PMDA used is therefore equal to the concentration of epoxy groups present in the feed of PLA15 through MMT. On the contrary PLA14 has no epoxy groups deriving from MMT.During the bulk polymerization of lactide, PMDA behaves as a tetrafunctional acid comonomer, because anhydride moieties react after nucleophilic attack of –OH groups of PLA growing chains and the other two carboxyl functions, which arise after the ring opening of anhydride, can react during the SSP process, where operating conditions allow shifting the equilibrium of the reaction, with –OH groups deriving either by subsequent opening of epoxide groups of the silane (PLA15) or by –OH end groups of PLA chains, as reported in Figures6 and 7; out of clarity, in these two figures only two chains growing from PMDA are shown: other chains behave in the same way.Figure 6
Possible structures of PLA nanocomposites branched with PMDA containing silane-modified MMT chemically linked to the polymer.Figure 7
Structure of PLA nanocomposites branched with PMDA containing unmodified MMT.The presence of a multifunctional reagent such as PMDA should result in two different behaviours of PLA14 and PLA15: PLA14, having no silane, has a marked shear thinning behavior, but it is anyway possible to determine its zero shear viscosity (η0=1.88∗104 Pa∗s). The sample is soluble in CH2Cl2, indicating that no cross-linking has occurred, but only partial branching of the macromolecular chains. PLA15, on the contrary, is not soluble in methylene chloride and melt viscosity has no plateau at low shear rates: this behavior is typical of highly branched and/or partially crosslinked polymers (Figure 8). This clearly indicates that there has been a reaction between the epoxy functions of organosilane with –OH groups of the growing chains.Figure 8
Rheological curves of PLA nanocomposites with PMDA compared with STD sample.


### 3.4. Thermal Analyses (DSC)

Figure9 reports DSC thermogram of STD PLA compared to PLA1, PLA2, and PLA3 having, respectively, 1-0.5-0.1% w/w of MMT. STD sample crystallizes on heating (cold crystallization) giving a crystalline phase that is characterized by two melting peaks. It has already been reported that the double melting behaviour can be linked to the formation of two different crystal forms: the α-one-pseudo-orthorhombic, pseudo-hexagonal, or orthorhombic (melting at higher temperature) and the β-one-orthorhombic or trigonal [35]. The most common polymorph is the α-form while the packing of β-form has been interpreted as an imperfect crystal structure. The helical conformations of the chains in the α- and β-structures have approximately the same energy, and thus their assembling must be the main reason for the existence of two different crystal structures [36].Figure 9
DSC thermograms of PLA and nanocomposites.On the other hand, it has been reported that the multiple melting behaviour in PLA could be also linked to a crystal reorganization upon melting, a fraction of imperfect crystals formed in melt crystallization which would have a high tendency to reorganize into more ordered structures and melt at higher temperature [36]. In this work, melt crystallization of STD is negligible, suggesting that the double melting behaviour observed cannot be attributed to a melt crystallization phenomenon but rather to the presence of both α-form, which is predominant, and β-form.Table6 summarizes thermal data for STD PLA and PLA/MMT nanocomposites with no silane. In the table χc indicates the crystalline fraction of the samples that was evaluated using (2); transition temperatures are taken according to Figure 1. Tg is glass transition temperature, ΔCp is the specific heat, Tcc is the cold crystallization temperature, ΔHcc is the cold crystallization enthalpy, Tm is melting temperature, ΔHm is melting enthalpy, Tc is melt crystallization temperature, and ΔHc is melt crystallization enthalpy as indicated in Materials and Methods.Table 6
DSC data of STD PLA and PLA nanocomposites with no GF80.
Sample
T
g (°C)
Δ
C
p (J/gK)
χ
c (%)
T
cc (°C)
T
cc onset (°C)
T
cc endset (°C)
Δ
H
cc (J/g)
T
m (°C)
Δ
H
m (J/g)
T
c (°C)
T
c onset (°C)
T
c endset (°C)
Δ
H
c (J/g)
STD
56.2
0.50
—
116.2
102.1
128.3
44.3
168.0
44.6
—
—
—
—
PLA1
55.2
0.40
11.7
93.1
87.7
101.7
32.1
165.0
42.1
121.3
130.0
88.5
10.8
PLA2
56.7
0.40
4.6
104.9
96.2
113.5
41.4
170.9
44.6
98.9
116.6
81.4
4.3
PLA3
60.9
0.46
2.3
114.2
102.5
125.3
40.6
174.4
40.8
98.1
113.1
82.3
2.1


#### 3.4.1. PLA1–PLA3:Tc and χc

T
c is absent in STD; unmodified MMT enhances the crystallization process and increases χc as the content of MMT increases: a small melt crystallization peak becomes visible (Figure 9). Tc increases significantly as the quantity of MMT increases, going from 98.1°C (PLA3) to 121.3°C (PLA1) with a difference of 23.2°C; ΔHc is low in any case. As a conclusion, MMT promotes crystalline features of the nanocomposites, acting as heterogeneous crystalline promoter.


#### 3.4.2. PLA1–PLA3:Tg and ΔCp

The effect of different layered silicate nanoparticles onTg in polymer nanocomposites has been studied in several works where PLA nanocomposites are obtained via extrusion but results seem controversial: in some cases, Tg increases have been reported [37]; in others a decrease has been demonstrated [38] or no relevant influence has been observed [39]. In the present paper, Tg of nanocomposites lowers as the quantity of MMT increases: in PLA3 glass transition is 4.7°C higher than in STD but in PLA1 it becomes 1.0°C lower than in STD.Higher MMT quantities tend also to decreaseΔCp: with low amounts of MMT, as in PLA3, ΔCp is close to STD getting lower for PLA2 and PLA1. As expected, higher χc causes lower ΔCp of the glass transition.


#### 3.4.3. PLA1–PLA3:Tcc and Tm

T
c
c lowers as MMT content increases: in PLA3 Tcc and Tcc onset and endset are similar to STD whereas for PLA1 there is a decrease of Tcc of 23.1°C in comparison to STD. The presence of MMT results also in lower Tm as MMT content increases in comparison with STD. These phenomena are reasonably due to a different crystallization process caused by the presence of MMT tallies; analogous trends have been already observed in a previous work [40].Thermal data of PLA4–PLA12, containing silane-modified MMT, are shown in Table7. DSC thermograms of PLA4, PLA7, and PLA10 and PLA6, PLA9, and PLA12 are reported in Supporting Information (S3 andS4).Table 7
DSC data of PLA nanocomposites with GF80 obtained by second heating curves.
Sample
T
g (°C)
Δ
C
p (J/gK)
χ
c (%)
T
cc  (°C)
T
cc onset  (°C)
T
cc endset  (°C)
Δ
H
cc (J/g)
T
m  (°C)
Δ
H
m (J/g)
T
c (°C)
T
c onset (°C)
T
c endset (°C)
Δ
H
c (J/g)
STD
56.2
0.50
—
116.2
102.1
128.3
44.3
168.0
44.6
—
—
—
—
PLA4
55.2
0.37
18.9
103.0
90.6
111.5
27.3
169.9
47.7
98.7
117.8
80.7
17.4
PLA5
59.9
0.46
2.5
114.2
102.5
125.9
40.2
174.4
41.0
98.0
113.3
81.5
2.3
PLA6
51.8
0.36
12.5
93.1
87.7
101.6
31.2
165.0
42.7
121.3
130.3
87.7
11.6
PLA7
54.7
0.32
10.9
100.7
91.6
107.7
32.8
168.3
42.9
96.7
109.2
80.5
10.0
PLA8
53.2
0.41
6.8
96.8
91.6
101.4
36.5
168.7
44.6
98.3
129.2
87.6
6.3
PLA9
53.1
0.37
9.4
95.2
90.2
100.7
33.5
166.3
42.3
124.6
130.7
110.9
8.7
PLA10
55.0
0.49
2.6
103.9
96.5
111.2
48.6
168.8
49.7
100.4
113.5
83.7
2.3
PLA11
57.1
0.36
1.4
110.4
100.5
125.3
35.4
175.1
36.0
99.8
110.2
82.8
1.3
PLA12
53.3
0.33
10.0
98.9
93.1
104.5
31.5
167.9
42.7
123.4
130.2
102.5
9.3


#### 3.4.4. PLA4–PLA12:Tc and χc

In all nanocomposites, melt crystallization peak is visible with an increase ofχc content with respect to STD sample: low quantities of MMT allow for high Tc that lowers as the quantity of MMT increases. This trend is opposite to that of PLA1, PLA2, and PLA3. This is probably due to the enhanced dispersion of silane modified MMT that increases surface area of the mineral making it a very effective heterogeneous crystallization promoter.


#### 3.4.5. PLA4–PLA12:Tg and ΔCp

When silane is present, low amounts of MMT, namely, PLA6, PLA9, and PLA12, do not increase glass transition in comparison to STD as happening for PLA3. Increasing the quantity of MMT,Tg increases but not significantly. In all samples, ΔCp is lower than that of STD as already seen for PLA1–PLA3.


#### 3.4.6. PLA4–PLA12:Tcc and Tm

T
c
c in all samples of Table 7 is lower than in STD; when no silane is present (PLA1-PLA2-PLA3), the lower the quantity of MMT, the higher the Tcc. When silane is present on the surface of MMT, the opposite trend is seen: Tcc is higher with 0.5% and 1% of MMT. No real trend can be observed regarding melt behaviour: in general, it seems that, for samples with the same quantity of silane, Tm tends to decrease as MMT content decreases.As a general consideration, in all nanocomposite samples a melt crystallization peak, that is absent in STD, is visible; bothTc and Tcc are significantly affected by the presence of silane, showing that very small quantities of modified MMT promote these processes.Silane, enhancing the dispersion of MMT, contributes to making it a very effective heterogeneous crystallization promoter, slightly increasing crystalline fraction of the nanocomposites.


### 3.5. Thermogravimetric Analyses (TGA)

Thermogravimetric analyses were performed both on MMT and on PLA nanocomposites. TGA was performed on MMT to check the validity of the results obtained via potentiometric titration of the silane; PLA nanocomposites were analysed to evaluate their resistance to thermal degradation.


#### 3.5.1. TGA on MMTs

Analyses were performed on pure and on silane-modified MMTs (Figure10).Figure 10
TGA curves of Cloisite 15A modified with different amounts of GF80.Weight loss is directly proportional to the quantity of silane present on MMT, in accordance with potentiometric titration results (Table8 and Figure 10).Table 8
Amount of silane present on Cloisite 15A surface and its weight loss.
Silane added(w/w % on MMT)
meq/kg(titration)
Weight loss (%) at 900°C
Δ Weight loss (%) with respect to unmodified MMT
MW of the residue(g/mol)
Cloisite 15A
—
44.49
—
—
2% GF80
119
45.22
0.73
61.34
7.5% GF80
380
46.67
2.18
57.37
15% GF80
712
48.72
4.23
59.41In Figure11 a correlation between amount of silane determined via potentiometric titration and weight loss is reported; variance value (R2=0.9991) suggests that titration and TGA data are in very good agreement with each other. Thanks to the combined use of titration and TGA, it is possible to determine the molecular weight of TGA residues calculated from Δ weight loss (%) with respect to unmodified MMT, which are in the range between 57.37 and 61.34 g/mol; these values suggest that only the inorganic part of the silane, represented by SiO2 (60.08 g/mol), remains when reaching high temperatures.Figure 11
Correlation between amount and silane weight loss on Cloisite 15A surface.


#### 3.5.2. TGA on PLA Nanocomposites

Many authors considered several molecular as well as radical mechanisms to explain PLA thermal degradation: according to McNeill and Leiper [41], the main reaction route is a nonradical, backbiting ester interchange reaction involving –OH chain ends. This reaction mechanism can, depending upon the size of the cyclic transition state, produce oligomers or acetaldehyde plus carbon monoxide.Kopinke et al. [42] also propose a radical reaction which starts either with an alkyl-oxygen or with an acyl-oxygen hemolysis involving the formation of several types of oxygen- and carbon-centered macroradicals plus carbon monoxide.Besides, several works [43, 44] reported that the addition of layered silicate nanoparticles, such as MMT, to PLA can influence thermal properties, mainly thermal degradation, in comparison to the unfilled matrix and that the presence of organic ions between the lamellae, especially at higher clay content, accelerates PLA degradation process, probably due to catalysis by the hydroxyl groups belonging to the silicate layers surface and by the organic modifier [45].Thermal stabilities of STD, PLA1, PLA2, and PLA3 were estimated evaluating temperatures corresponding to 1%, 10%, 50%, and 95% of weight loss (T1%, T10%, T50%, and T95%); results obtained are reported in Table 9. TGA curves of STD and PLA1, PLA2, and PLA3 are presented in Supporting Information (S5).Table 9
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA1
257.0
296.0
320.8
337.8
PLA2
249.1
287.6
311.6
329.3
PLA3
268.8
295.5
320.2
338.4Thermal stability in comparison to STD decreases: both the beginning of degradation (T1%) and the end (T95%) occur at lower temperature. The decrease of thermal stability probably is due to both the presence of more –OH chain ends in samples with lower molecular weights in comparison to STD and the interaction with surface –OH of unmodified MMT.Thermal data of PLA nanocomposites containing silane-modified MMT are reported in Table10. TGA curves of PLA4–12 are shown in Supporting Information (S6 andS7).Table 10
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA4
245.4
277.1
304.6
321.1
PLA5
289.5
339.8
382.8
400.4
PLA6
300.1
350.4
386.1
403.0
PLA7
243.5
279.2
309.6
327.0
PLA8
321.1
361.7
386.0
400.3
PLA9
323.9
348.8
375.0
400.0
PLA10
299.0
346.5
364.5
382.8
PLA11
303.2
325.4
367.0
386.0
PLA12
324.6
351.6
368.9
386.3T
1
% of PLA8 (7.5% w/w silane/MMT) is 45.9°C higher than that of STD and T10% is still very high (42.3°C higher than STD); PLA8, PLA9, PLA10, PLA11, and PLA12 show marked increases of thermal stability in the range of T1%–T95% in comparison to STD. The higher degradation temperature in comparison with PLA1, PLA2, and PLA3 can be explained considering that there are less –OH chain ends able to be involved in the backbiting ester interchange reaction and that there is no interaction of surface –OH from modified MMT due to the presence of organosilane.As a general statement, all samples with modified MMT, except for PLA4 and PLA7, show higher thermal stability in comparison to STD:T1% and T10% increase as silane content increases, indicating that thermal stability is promoted by the silane. The lower thermal stability of PLA4 and PLA7 can be explained considering that these samples have high MMT content (1% w/w) and relatively low amounts of silane on the surface. This implies that MMT platelets still have –OH moieties on the surface promoting degradation and at the same time, being better dispersed than PLA1, a high surface area in contact with the polymeric matrix. The combination of these two factors, –OH groups available on the surface and high surface area in contact with the polymer, determines lower thermal stability in comparison to both STD and other modified PLA nanocomposites.


### 3.6. Rheological Analyses

Rheological curves obtained via frequency sweep experiments on STD, PLA1, PLA2, and PLA3 are presented in Figure12.Figure 12
Rheological curves of STD and PLA1, PLA2, and PLA3.Curves have viscoelastic behaviour, with a Newtonian plateau at low shear rates and shear thinning behaviour. Zero shear viscosity values,η0 (shown in Table 11), have been calculated using Cross equation (3) passing from experimental data obtained as complex viscosity versus angular frequency to data as standard shear viscosity versus shear rate thanks to Cox-Merz rule.Table 11
Zero shear viscosity of PLA nanocomposites.
Sample
η
0 (Pa ∗ s)
STD
1.19∗ 103
PLA1
5.96∗ 103
PLA2
4.38∗ 103
PLA3
3.31∗ 103
PLA4
8.42∗ 103
PLA5
7.63∗ 103
PLA6
5.96∗ 103
PLA7
4.5∗ 103
PLA8
4.3∗ 103
PLA9
3.6∗ 103
PLA10
68.2∗ 103
PLA11
62.3∗ 103
PLA12
56.7∗ 103In Cross equation,η0 represents zero shear viscosity, η∞ is infinite-shear viscosity, γ˙ is shear rate, (1-n) is known as Cross rate constant (n is non-Newtonian behaviour index), it is dimensionless and is a measure of the degree of dependence of viscosity on shear rate in the shear thinning region, and K is known as the Cross time constant:(3)η-η∞η0-η∞=11+K2·γ˙21-n/2=11+K·γ˙1-n.Figure 12 shows that the presence of MMT consistently increases the viscosity of the melt even if SEC shows that the soluble part of PLA1–PLA3 has molecular weights far lower than those of STD. η0 is much higher and increases considerably as MMT content increases.Bearing in mind that SEC data refer only to the polymer dissolved, and therefore only to the polymer that is not chemically bonded to the nanoparticles, the high values ofη0 of unmodified samples can be due to –C=O groups of PLA that alter the normal flow of STD PLA, flowing with higher difficulty in the direction of flow and promoting the formation of a percolating network derived from the reciprocity among the strong relating sheet particles as a result of the preferential orientation of MMT layers [46].It is important to underline that, thanks to in situ synthesis, the effects of MMT on melt viscosity are greatly enhanced. Wang et al. [47] studying melt compounding of commercial PLA and MMT reported that far higher quantities of MMT (>5% w/w) were required to reach viscosity values similar to those of neat PLA and also that the inclusion of small amounts of MMT (1% w/w) lowers the complex viscosity of PLA matrix. Using “in situ” synthesis, even 0.1% w/w of MMT allows obtaining melt viscosity values far higher than those of neat PLA. When silane is present on the surface of MMT (Figure 13), the effect on melt viscosity is magnified; melt viscosity at low shears further increases, and the shear thinning behaviour is enhanced. The effect in this case may be caused by the presence of a high number of stable covalent bonds between polymer macromolecules and the silane that at low shears create a sort of network responsible for increasing viscosity [48]. At higher shears the different surface energy of unmodified MMT and PLA creates aggregation between MMT nanoparticles and generates small voids that slightly contribute to building up viscosity for unmodified samples; when silane is present, bonds between polymer and silane act as compatibilizer and prevent the aggregation of MMT and the formation of interruptions, lowering melt viscosity.Figure 13
Rheological curves of STD PLA and modified samples.This variation in melt viscosity is obtained thanks to the improved compatibility between MMT and the polymeric matrix and thanks to the quantity of MMT platelets. Besides, the increase is correlated with the structure of nanocomposites. In fact, high melt viscosities are obtained in polymer nanocomposites with fully exfoliated clay minerals with high aspect ratio that orient lamellae in the direction of flow [49], as reported in Figure 14.Figure 14
Schematic representation of MMT lamellae in PLA nanocomposites with free orientation (1) and in the direction of flow (2).


## 3.1. WAXS Analyses

Crystalline peaks of MMT powder with different amounts of GF80 (2%–7.5%–15%) were studied in order to understand if silane contributes to increasing the interlayer space between the lamellae. Neat MMT exhibits four main diffraction peaks: the major one at2θ=19.77° and three minor ones at 7.19°, 35.31°, and 54.24°, attributed to the reflections of the four crystal planes of MMT. When silane is present, all the four peaks are still visible (Table 4) and each of them has the tendency to shift to lower angles in comparison to pure MMT, as Figure 2 evidences (only peak 2 is almost unaffected), promoting exfoliation.Table 4
2θ values of neat MMT and modified MMT.
Diffraction peak
Neat MMT2θ  [°]
MMT − 2%w/w GF802θ  [°]
MMT − 7.5%w/w GF802θ  [°]
MMT − 15%w/w GF802θ  [°]
1
7.19
6.87
6.87
6.47
2
19.77
19.73
19.79
19.76
3
35.31
35.06
35.12
34.86
4
54.24
53.85
54.12
53.98Figure 2
WAXS diffractograms of unmodified MMT (red), MMT with 2% w/w GF80 (blue), MMT with 7.5% w/w GF80 (green), and MMT with 15% w/w GF80 (violet).According to Bragg’s law (equation (1)), lower 2θ indicates an increase in the distance of the diffraction planes, that is, an increase in the basal spacing. Neat MMT presents a single basal peak at 7.19° (2θ), corresponding to a d001-spacing of 12.28 Å, which is the basal space distance of the natural clay [30]. The patterns of MMT samples modified with different amounts of silane show basal reflections at 6.87° (d001-spacing = 12.86 Å) in the case of MMT − 2% and MMT − 7.5% and at 6.47° (d001-spacing = 13.65 Å) for MMT − 15%, indicating an increase in the distance of the diffraction planes of 0.58 Å and 1.37 Å, respectively. This phenomenon reveals that some intergallery expansion has taken place thanks to the presence of silane and the fact that the higher the quantity of silane the higher the spacing between lamellae.WAXS analyses were used also to determine the crystalline structure of nanocomposite PLAs: the analysis was performed on the films obtained from casting as described in Section2.1. WAXS patterns of MMT, of STD PLA, and of PLA containing 1.0% w/w and 0.1% w/w of unmodified MMT (PLA1 and PLA3, resp.), collected in the range of 2θ = 5–60°, are presented in Figure 3. In PLA1 and PLA3 a diffraction peak is present, at 2θ = 16.82° and 16.94°, respectively, consistent with the major crystalline peak of highly crystalline PLA [31].Figure 3
WAXS diffractograms of Cloisite 15A powder, STD PLA, PLA1, and PLA3.It is possible to observe an increase of the height of the diffraction peak as the amount of MMT increases. This behavior indicates that MMT promotes heteronucleation process.Figure4 shows WAXS patterns of STD PLA and of PLA with 1% w/w of modified MMT with 2% w/w of GF80 (PLA4) and with 15% w/w of GF80 (PLA10). The nanocomposites patterns show that diffraction peaks of PLA4 and PLA10 are higher than STD; this behavior indicates that modified MMT promotes the intercalation of MMT in PLA chains.Figure 4
WAXS diffractograms of STD PLA, PLA4, and PLA10.


## 3.2. TEM Images

Figure5 reports TEM images of PLA nanocomposites; in PLA1, unmodified MMT is dispersed in the polymeric matrix, with aggregates having big dimensions indicating that the mineral has not been efficiently exfoliated. A good exfoliation should result in a good dispersion of MMT platelets within the polymeric matrix, each platelet having a length of about 100–200 nm, a similar width, and a thickness of some nanometers [32, 33]. In Figure 5, the effect of silane is visible: as its quantity increases, the dispersion of MMT platelets is enhanced. In PLA1 an aggregate is shown having big dimensions (maximum length = 1.6 μm, width 500 nm): similar aggregates are scattered through the nanocomposite. In PLA4, aggregates are present together with better exfoliated platelets: the bigger aggregate (number 1) has a length of about 1 μm and width of about 500 nm. Other big aggregates (number 2) are about 500 nm × 100 nm or less: other particles have an average length of 154±100 nm and an average width of 41±25 nm (calculated on 20 particles). In PLA7 aggregates with lower dimension are visible, with the bigger one (number 1) being about 500 nm × 130 nm: average length is 122±55 nm and width is 38±18 nm. In PLA4 and PLA7 the presence of some aggregates influences the dispersity of data collected. In Supporting Information, images of PLA4 (seeS1in Supplementary Material available online at http://dx.doi.org/10.1155/2015/418418) and PLA7 (S2) with lower magnification are presented. In PLA10, MMT is homogeneously dispersed and no big aggregates are visible: average length is 110±40 nm; average width is 33±15 nm.Figure 5
TEM images 1% w/w of PLA1 (a), PLA7 (b), PLA4 (c), and PLA10 (d).
(a)
(b)
(c)
(d)


## 3.3. Size Exclusion Chromatography (SEC)

Numeral average molecular weights (Mn-) and molecular weight distribution (D) determined via SEC and expressed as polystyrene equivalents are provided in Table 5; as described in Section 2.1, samples were filtered with a 0.45 μm filter; therefore molecular weight data refer only to the polymer present in the solution.Table 5
SEC data of PLAs synthesized.
Sample
M
n
-
D
STD
54124
1.79
PLA1
29901
1.26
PLA2
28563
1.33
PLA3
33238
1.29
PLA4
59230
1.86
PLA5
57431
1.85
PLA6
53611
1.80
PLA7
61551
1.88
PLA8
62045
1.89
PLA9
62117
1.89
PLA10
59683
1.88
PLA11
58661
1.87
PLA12
59342
1.89
PLA13
53991
1.77Samples PLA1, PLA2, and PLA3, containing unmodified MMT, show that the presence of pure MMT interferes with the polymerization process, lowering the molecular weights as the quantity of mineral increases. Two possible explanations for this phenomenon can be given. The first one is related to the fact that –OH groups on the surface of unmodified MMT can potentially initiate the polymerization, as already reported in literature [34]. Since molecular weight distribution values of PLA1, PLA2, and PLA3 are much lower than that of STD, a second possible explanation, alternative to the first one, is related to the fact that the free acidic sites of unmodified MMT may slow the kinetics of polymerization process partially deactivating the catalyst. The lower activity of catalyst decreases the kinetics of ROP but also the kinetics of transesterification reaction that is the cause of polydispersity increase.PLA13, containing a very high quantity of catalyst (3% w/w) and of MMT (5% w/w), was synthesised to confirm the validity of one of these hypotheses: SEC analysis shows thatMn- and D of PLA13 are very close to those of STD sample (Mn-: 53991; D: 1.77). These values demonstrate that pure MMT has the tendency to deactivate part of the catalyst, since higher amounts of tin octanoate lead to a PLA with high molecular weight; the second hypothesis is therefore confirmed.Nanocomposites containing silane-modified MMT haveMn- comparable with that of pure PLAs even when only 2% w/w of silane is used. Molecular weights tend to increase as the quantity of silane increases, indicating that epoxy silane reacting with MMT –OH surface groups decreases the interaction of MMT with catalyst.Since SEC refers only to the polymer that is present in solution, two samples were synthesized to confirm the reaction between epoxy silane and end groups of the growing polymeric chain: one using the same feed and conditions of PLA3 (named PLA14) and one using the same feed and conditions of PLA12 (named PLA15); in both PLA14 and PLA15 a tetrafunctional comonomer, pyromellitic dianhydride (PMDA,3.56∗10-5 mol in 50 g of lactide), was added in the feed. In PLA15, 0.1% w/w on lactide of MMT having 712 meq/kg of silane (i.e., 712 meq/kg of epoxy groups, see Table 1) is introduced in the feed. This means that the concentration of epoxy groups deriving from silane-modified MMT is 0.712 meq/kg of lactide (i.e., 3.56∗10-5 mol in 50 g of lactide). The concentration of PMDA used is therefore equal to the concentration of epoxy groups present in the feed of PLA15 through MMT. On the contrary PLA14 has no epoxy groups deriving from MMT.During the bulk polymerization of lactide, PMDA behaves as a tetrafunctional acid comonomer, because anhydride moieties react after nucleophilic attack of –OH groups of PLA growing chains and the other two carboxyl functions, which arise after the ring opening of anhydride, can react during the SSP process, where operating conditions allow shifting the equilibrium of the reaction, with –OH groups deriving either by subsequent opening of epoxide groups of the silane (PLA15) or by –OH end groups of PLA chains, as reported in Figures6 and 7; out of clarity, in these two figures only two chains growing from PMDA are shown: other chains behave in the same way.Figure 6
Possible structures of PLA nanocomposites branched with PMDA containing silane-modified MMT chemically linked to the polymer.Figure 7
Structure of PLA nanocomposites branched with PMDA containing unmodified MMT.The presence of a multifunctional reagent such as PMDA should result in two different behaviours of PLA14 and PLA15: PLA14, having no silane, has a marked shear thinning behavior, but it is anyway possible to determine its zero shear viscosity (η0=1.88∗104 Pa∗s). The sample is soluble in CH2Cl2, indicating that no cross-linking has occurred, but only partial branching of the macromolecular chains. PLA15, on the contrary, is not soluble in methylene chloride and melt viscosity has no plateau at low shear rates: this behavior is typical of highly branched and/or partially crosslinked polymers (Figure 8). This clearly indicates that there has been a reaction between the epoxy functions of organosilane with –OH groups of the growing chains.Figure 8
Rheological curves of PLA nanocomposites with PMDA compared with STD sample.


## 3.4. Thermal Analyses (DSC)

Figure9 reports DSC thermogram of STD PLA compared to PLA1, PLA2, and PLA3 having, respectively, 1-0.5-0.1% w/w of MMT. STD sample crystallizes on heating (cold crystallization) giving a crystalline phase that is characterized by two melting peaks. It has already been reported that the double melting behaviour can be linked to the formation of two different crystal forms: the α-one-pseudo-orthorhombic, pseudo-hexagonal, or orthorhombic (melting at higher temperature) and the β-one-orthorhombic or trigonal [35]. The most common polymorph is the α-form while the packing of β-form has been interpreted as an imperfect crystal structure. The helical conformations of the chains in the α- and β-structures have approximately the same energy, and thus their assembling must be the main reason for the existence of two different crystal structures [36].Figure 9
DSC thermograms of PLA and nanocomposites.On the other hand, it has been reported that the multiple melting behaviour in PLA could be also linked to a crystal reorganization upon melting, a fraction of imperfect crystals formed in melt crystallization which would have a high tendency to reorganize into more ordered structures and melt at higher temperature [36]. In this work, melt crystallization of STD is negligible, suggesting that the double melting behaviour observed cannot be attributed to a melt crystallization phenomenon but rather to the presence of both α-form, which is predominant, and β-form.Table6 summarizes thermal data for STD PLA and PLA/MMT nanocomposites with no silane. In the table χc indicates the crystalline fraction of the samples that was evaluated using (2); transition temperatures are taken according to Figure 1. Tg is glass transition temperature, ΔCp is the specific heat, Tcc is the cold crystallization temperature, ΔHcc is the cold crystallization enthalpy, Tm is melting temperature, ΔHm is melting enthalpy, Tc is melt crystallization temperature, and ΔHc is melt crystallization enthalpy as indicated in Materials and Methods.Table 6
DSC data of STD PLA and PLA nanocomposites with no GF80.
Sample
T
g (°C)
Δ
C
p (J/gK)
χ
c (%)
T
cc (°C)
T
cc onset (°C)
T
cc endset (°C)
Δ
H
cc (J/g)
T
m (°C)
Δ
H
m (J/g)
T
c (°C)
T
c onset (°C)
T
c endset (°C)
Δ
H
c (J/g)
STD
56.2
0.50
—
116.2
102.1
128.3
44.3
168.0
44.6
—
—
—
—
PLA1
55.2
0.40
11.7
93.1
87.7
101.7
32.1
165.0
42.1
121.3
130.0
88.5
10.8
PLA2
56.7
0.40
4.6
104.9
96.2
113.5
41.4
170.9
44.6
98.9
116.6
81.4
4.3
PLA3
60.9
0.46
2.3
114.2
102.5
125.3
40.6
174.4
40.8
98.1
113.1
82.3
2.1


### 3.4.1. PLA1–PLA3:Tc and χc

T
c is absent in STD; unmodified MMT enhances the crystallization process and increases χc as the content of MMT increases: a small melt crystallization peak becomes visible (Figure 9). Tc increases significantly as the quantity of MMT increases, going from 98.1°C (PLA3) to 121.3°C (PLA1) with a difference of 23.2°C; ΔHc is low in any case. As a conclusion, MMT promotes crystalline features of the nanocomposites, acting as heterogeneous crystalline promoter.


### 3.4.2. PLA1–PLA3:Tg and ΔCp

The effect of different layered silicate nanoparticles onTg in polymer nanocomposites has been studied in several works where PLA nanocomposites are obtained via extrusion but results seem controversial: in some cases, Tg increases have been reported [37]; in others a decrease has been demonstrated [38] or no relevant influence has been observed [39]. In the present paper, Tg of nanocomposites lowers as the quantity of MMT increases: in PLA3 glass transition is 4.7°C higher than in STD but in PLA1 it becomes 1.0°C lower than in STD.Higher MMT quantities tend also to decreaseΔCp: with low amounts of MMT, as in PLA3, ΔCp is close to STD getting lower for PLA2 and PLA1. As expected, higher χc causes lower ΔCp of the glass transition.


### 3.4.3. PLA1–PLA3:Tcc and Tm

T
c
c lowers as MMT content increases: in PLA3 Tcc and Tcc onset and endset are similar to STD whereas for PLA1 there is a decrease of Tcc of 23.1°C in comparison to STD. The presence of MMT results also in lower Tm as MMT content increases in comparison with STD. These phenomena are reasonably due to a different crystallization process caused by the presence of MMT tallies; analogous trends have been already observed in a previous work [40].Thermal data of PLA4–PLA12, containing silane-modified MMT, are shown in Table7. DSC thermograms of PLA4, PLA7, and PLA10 and PLA6, PLA9, and PLA12 are reported in Supporting Information (S3 andS4).Table 7
DSC data of PLA nanocomposites with GF80 obtained by second heating curves.
Sample
T
g (°C)
Δ
C
p (J/gK)
χ
c (%)
T
cc  (°C)
T
cc onset  (°C)
T
cc endset  (°C)
Δ
H
cc (J/g)
T
m  (°C)
Δ
H
m (J/g)
T
c (°C)
T
c onset (°C)
T
c endset (°C)
Δ
H
c (J/g)
STD
56.2
0.50
—
116.2
102.1
128.3
44.3
168.0
44.6
—
—
—
—
PLA4
55.2
0.37
18.9
103.0
90.6
111.5
27.3
169.9
47.7
98.7
117.8
80.7
17.4
PLA5
59.9
0.46
2.5
114.2
102.5
125.9
40.2
174.4
41.0
98.0
113.3
81.5
2.3
PLA6
51.8
0.36
12.5
93.1
87.7
101.6
31.2
165.0
42.7
121.3
130.3
87.7
11.6
PLA7
54.7
0.32
10.9
100.7
91.6
107.7
32.8
168.3
42.9
96.7
109.2
80.5
10.0
PLA8
53.2
0.41
6.8
96.8
91.6
101.4
36.5
168.7
44.6
98.3
129.2
87.6
6.3
PLA9
53.1
0.37
9.4
95.2
90.2
100.7
33.5
166.3
42.3
124.6
130.7
110.9
8.7
PLA10
55.0
0.49
2.6
103.9
96.5
111.2
48.6
168.8
49.7
100.4
113.5
83.7
2.3
PLA11
57.1
0.36
1.4
110.4
100.5
125.3
35.4
175.1
36.0
99.8
110.2
82.8
1.3
PLA12
53.3
0.33
10.0
98.9
93.1
104.5
31.5
167.9
42.7
123.4
130.2
102.5
9.3


### 3.4.4. PLA4–PLA12:Tc and χc

In all nanocomposites, melt crystallization peak is visible with an increase ofχc content with respect to STD sample: low quantities of MMT allow for high Tc that lowers as the quantity of MMT increases. This trend is opposite to that of PLA1, PLA2, and PLA3. This is probably due to the enhanced dispersion of silane modified MMT that increases surface area of the mineral making it a very effective heterogeneous crystallization promoter.


### 3.4.5. PLA4–PLA12:Tg and ΔCp

When silane is present, low amounts of MMT, namely, PLA6, PLA9, and PLA12, do not increase glass transition in comparison to STD as happening for PLA3. Increasing the quantity of MMT,Tg increases but not significantly. In all samples, ΔCp is lower than that of STD as already seen for PLA1–PLA3.


### 3.4.6. PLA4–PLA12:Tcc and Tm

T
c
c in all samples of Table 7 is lower than in STD; when no silane is present (PLA1-PLA2-PLA3), the lower the quantity of MMT, the higher the Tcc. When silane is present on the surface of MMT, the opposite trend is seen: Tcc is higher with 0.5% and 1% of MMT. No real trend can be observed regarding melt behaviour: in general, it seems that, for samples with the same quantity of silane, Tm tends to decrease as MMT content decreases.As a general consideration, in all nanocomposite samples a melt crystallization peak, that is absent in STD, is visible; bothTc and Tcc are significantly affected by the presence of silane, showing that very small quantities of modified MMT promote these processes.Silane, enhancing the dispersion of MMT, contributes to making it a very effective heterogeneous crystallization promoter, slightly increasing crystalline fraction of the nanocomposites.


## 3.4.1. PLA1–PLA3:Tc and χc

T
c is absent in STD; unmodified MMT enhances the crystallization process and increases χc as the content of MMT increases: a small melt crystallization peak becomes visible (Figure 9). Tc increases significantly as the quantity of MMT increases, going from 98.1°C (PLA3) to 121.3°C (PLA1) with a difference of 23.2°C; ΔHc is low in any case. As a conclusion, MMT promotes crystalline features of the nanocomposites, acting as heterogeneous crystalline promoter.


## 3.4.2. PLA1–PLA3:Tg and ΔCp

The effect of different layered silicate nanoparticles onTg in polymer nanocomposites has been studied in several works where PLA nanocomposites are obtained via extrusion but results seem controversial: in some cases, Tg increases have been reported [37]; in others a decrease has been demonstrated [38] or no relevant influence has been observed [39]. In the present paper, Tg of nanocomposites lowers as the quantity of MMT increases: in PLA3 glass transition is 4.7°C higher than in STD but in PLA1 it becomes 1.0°C lower than in STD.Higher MMT quantities tend also to decreaseΔCp: with low amounts of MMT, as in PLA3, ΔCp is close to STD getting lower for PLA2 and PLA1. As expected, higher χc causes lower ΔCp of the glass transition.


## 3.4.3. PLA1–PLA3:Tcc and Tm

T
c
c lowers as MMT content increases: in PLA3 Tcc and Tcc onset and endset are similar to STD whereas for PLA1 there is a decrease of Tcc of 23.1°C in comparison to STD. The presence of MMT results also in lower Tm as MMT content increases in comparison with STD. These phenomena are reasonably due to a different crystallization process caused by the presence of MMT tallies; analogous trends have been already observed in a previous work [40].Thermal data of PLA4–PLA12, containing silane-modified MMT, are shown in Table7. DSC thermograms of PLA4, PLA7, and PLA10 and PLA6, PLA9, and PLA12 are reported in Supporting Information (S3 andS4).Table 7
DSC data of PLA nanocomposites with GF80 obtained by second heating curves.
Sample
T
g (°C)
Δ
C
p (J/gK)
χ
c (%)
T
cc  (°C)
T
cc onset  (°C)
T
cc endset  (°C)
Δ
H
cc (J/g)
T
m  (°C)
Δ
H
m (J/g)
T
c (°C)
T
c onset (°C)
T
c endset (°C)
Δ
H
c (J/g)
STD
56.2
0.50
—
116.2
102.1
128.3
44.3
168.0
44.6
—
—
—
—
PLA4
55.2
0.37
18.9
103.0
90.6
111.5
27.3
169.9
47.7
98.7
117.8
80.7
17.4
PLA5
59.9
0.46
2.5
114.2
102.5
125.9
40.2
174.4
41.0
98.0
113.3
81.5
2.3
PLA6
51.8
0.36
12.5
93.1
87.7
101.6
31.2
165.0
42.7
121.3
130.3
87.7
11.6
PLA7
54.7
0.32
10.9
100.7
91.6
107.7
32.8
168.3
42.9
96.7
109.2
80.5
10.0
PLA8
53.2
0.41
6.8
96.8
91.6
101.4
36.5
168.7
44.6
98.3
129.2
87.6
6.3
PLA9
53.1
0.37
9.4
95.2
90.2
100.7
33.5
166.3
42.3
124.6
130.7
110.9
8.7
PLA10
55.0
0.49
2.6
103.9
96.5
111.2
48.6
168.8
49.7
100.4
113.5
83.7
2.3
PLA11
57.1
0.36
1.4
110.4
100.5
125.3
35.4
175.1
36.0
99.8
110.2
82.8
1.3
PLA12
53.3
0.33
10.0
98.9
93.1
104.5
31.5
167.9
42.7
123.4
130.2
102.5
9.3


## 3.4.4. PLA4–PLA12:Tc and χc

In all nanocomposites, melt crystallization peak is visible with an increase ofχc content with respect to STD sample: low quantities of MMT allow for high Tc that lowers as the quantity of MMT increases. This trend is opposite to that of PLA1, PLA2, and PLA3. This is probably due to the enhanced dispersion of silane modified MMT that increases surface area of the mineral making it a very effective heterogeneous crystallization promoter.


## 3.4.5. PLA4–PLA12:Tg and ΔCp

When silane is present, low amounts of MMT, namely, PLA6, PLA9, and PLA12, do not increase glass transition in comparison to STD as happening for PLA3. Increasing the quantity of MMT,Tg increases but not significantly. In all samples, ΔCp is lower than that of STD as already seen for PLA1–PLA3.


## 3.4.6. PLA4–PLA12:Tcc and Tm

T
c
c in all samples of Table 7 is lower than in STD; when no silane is present (PLA1-PLA2-PLA3), the lower the quantity of MMT, the higher the Tcc. When silane is present on the surface of MMT, the opposite trend is seen: Tcc is higher with 0.5% and 1% of MMT. No real trend can be observed regarding melt behaviour: in general, it seems that, for samples with the same quantity of silane, Tm tends to decrease as MMT content decreases.As a general consideration, in all nanocomposite samples a melt crystallization peak, that is absent in STD, is visible; bothTc and Tcc are significantly affected by the presence of silane, showing that very small quantities of modified MMT promote these processes.Silane, enhancing the dispersion of MMT, contributes to making it a very effective heterogeneous crystallization promoter, slightly increasing crystalline fraction of the nanocomposites.


## 3.5. Thermogravimetric Analyses (TGA)

Thermogravimetric analyses were performed both on MMT and on PLA nanocomposites. TGA was performed on MMT to check the validity of the results obtained via potentiometric titration of the silane; PLA nanocomposites were analysed to evaluate their resistance to thermal degradation.


### 3.5.1. TGA on MMTs

Analyses were performed on pure and on silane-modified MMTs (Figure10).Figure 10
TGA curves of Cloisite 15A modified with different amounts of GF80.Weight loss is directly proportional to the quantity of silane present on MMT, in accordance with potentiometric titration results (Table8 and Figure 10).Table 8
Amount of silane present on Cloisite 15A surface and its weight loss.
Silane added(w/w % on MMT)
meq/kg(titration)
Weight loss (%) at 900°C
Δ Weight loss (%) with respect to unmodified MMT
MW of the residue(g/mol)
Cloisite 15A
—
44.49
—
—
2% GF80
119
45.22
0.73
61.34
7.5% GF80
380
46.67
2.18
57.37
15% GF80
712
48.72
4.23
59.41In Figure11 a correlation between amount of silane determined via potentiometric titration and weight loss is reported; variance value (R2=0.9991) suggests that titration and TGA data are in very good agreement with each other. Thanks to the combined use of titration and TGA, it is possible to determine the molecular weight of TGA residues calculated from Δ weight loss (%) with respect to unmodified MMT, which are in the range between 57.37 and 61.34 g/mol; these values suggest that only the inorganic part of the silane, represented by SiO2 (60.08 g/mol), remains when reaching high temperatures.Figure 11
Correlation between amount and silane weight loss on Cloisite 15A surface.


### 3.5.2. TGA on PLA Nanocomposites

Many authors considered several molecular as well as radical mechanisms to explain PLA thermal degradation: according to McNeill and Leiper [41], the main reaction route is a nonradical, backbiting ester interchange reaction involving –OH chain ends. This reaction mechanism can, depending upon the size of the cyclic transition state, produce oligomers or acetaldehyde plus carbon monoxide.Kopinke et al. [42] also propose a radical reaction which starts either with an alkyl-oxygen or with an acyl-oxygen hemolysis involving the formation of several types of oxygen- and carbon-centered macroradicals plus carbon monoxide.Besides, several works [43, 44] reported that the addition of layered silicate nanoparticles, such as MMT, to PLA can influence thermal properties, mainly thermal degradation, in comparison to the unfilled matrix and that the presence of organic ions between the lamellae, especially at higher clay content, accelerates PLA degradation process, probably due to catalysis by the hydroxyl groups belonging to the silicate layers surface and by the organic modifier [45].Thermal stabilities of STD, PLA1, PLA2, and PLA3 were estimated evaluating temperatures corresponding to 1%, 10%, 50%, and 95% of weight loss (T1%, T10%, T50%, and T95%); results obtained are reported in Table 9. TGA curves of STD and PLA1, PLA2, and PLA3 are presented in Supporting Information (S5).Table 9
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA1
257.0
296.0
320.8
337.8
PLA2
249.1
287.6
311.6
329.3
PLA3
268.8
295.5
320.2
338.4Thermal stability in comparison to STD decreases: both the beginning of degradation (T1%) and the end (T95%) occur at lower temperature. The decrease of thermal stability probably is due to both the presence of more –OH chain ends in samples with lower molecular weights in comparison to STD and the interaction with surface –OH of unmodified MMT.Thermal data of PLA nanocomposites containing silane-modified MMT are reported in Table10. TGA curves of PLA4–12 are shown in Supporting Information (S6 andS7).Table 10
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA4
245.4
277.1
304.6
321.1
PLA5
289.5
339.8
382.8
400.4
PLA6
300.1
350.4
386.1
403.0
PLA7
243.5
279.2
309.6
327.0
PLA8
321.1
361.7
386.0
400.3
PLA9
323.9
348.8
375.0
400.0
PLA10
299.0
346.5
364.5
382.8
PLA11
303.2
325.4
367.0
386.0
PLA12
324.6
351.6
368.9
386.3T
1
% of PLA8 (7.5% w/w silane/MMT) is 45.9°C higher than that of STD and T10% is still very high (42.3°C higher than STD); PLA8, PLA9, PLA10, PLA11, and PLA12 show marked increases of thermal stability in the range of T1%–T95% in comparison to STD. The higher degradation temperature in comparison with PLA1, PLA2, and PLA3 can be explained considering that there are less –OH chain ends able to be involved in the backbiting ester interchange reaction and that there is no interaction of surface –OH from modified MMT due to the presence of organosilane.As a general statement, all samples with modified MMT, except for PLA4 and PLA7, show higher thermal stability in comparison to STD:T1% and T10% increase as silane content increases, indicating that thermal stability is promoted by the silane. The lower thermal stability of PLA4 and PLA7 can be explained considering that these samples have high MMT content (1% w/w) and relatively low amounts of silane on the surface. This implies that MMT platelets still have –OH moieties on the surface promoting degradation and at the same time, being better dispersed than PLA1, a high surface area in contact with the polymeric matrix. The combination of these two factors, –OH groups available on the surface and high surface area in contact with the polymer, determines lower thermal stability in comparison to both STD and other modified PLA nanocomposites.


## 3.5.1. TGA on MMTs

Analyses were performed on pure and on silane-modified MMTs (Figure10).Figure 10
TGA curves of Cloisite 15A modified with different amounts of GF80.Weight loss is directly proportional to the quantity of silane present on MMT, in accordance with potentiometric titration results (Table8 and Figure 10).Table 8
Amount of silane present on Cloisite 15A surface and its weight loss.
Silane added(w/w % on MMT)
meq/kg(titration)
Weight loss (%) at 900°C
Δ Weight loss (%) with respect to unmodified MMT
MW of the residue(g/mol)
Cloisite 15A
—
44.49
—
—
2% GF80
119
45.22
0.73
61.34
7.5% GF80
380
46.67
2.18
57.37
15% GF80
712
48.72
4.23
59.41In Figure11 a correlation between amount of silane determined via potentiometric titration and weight loss is reported; variance value (R2=0.9991) suggests that titration and TGA data are in very good agreement with each other. Thanks to the combined use of titration and TGA, it is possible to determine the molecular weight of TGA residues calculated from Δ weight loss (%) with respect to unmodified MMT, which are in the range between 57.37 and 61.34 g/mol; these values suggest that only the inorganic part of the silane, represented by SiO2 (60.08 g/mol), remains when reaching high temperatures.Figure 11
Correlation between amount and silane weight loss on Cloisite 15A surface.


## 3.5.2. TGA on PLA Nanocomposites

Many authors considered several molecular as well as radical mechanisms to explain PLA thermal degradation: according to McNeill and Leiper [41], the main reaction route is a nonradical, backbiting ester interchange reaction involving –OH chain ends. This reaction mechanism can, depending upon the size of the cyclic transition state, produce oligomers or acetaldehyde plus carbon monoxide.Kopinke et al. [42] also propose a radical reaction which starts either with an alkyl-oxygen or with an acyl-oxygen hemolysis involving the formation of several types of oxygen- and carbon-centered macroradicals plus carbon monoxide.Besides, several works [43, 44] reported that the addition of layered silicate nanoparticles, such as MMT, to PLA can influence thermal properties, mainly thermal degradation, in comparison to the unfilled matrix and that the presence of organic ions between the lamellae, especially at higher clay content, accelerates PLA degradation process, probably due to catalysis by the hydroxyl groups belonging to the silicate layers surface and by the organic modifier [45].Thermal stabilities of STD, PLA1, PLA2, and PLA3 were estimated evaluating temperatures corresponding to 1%, 10%, 50%, and 95% of weight loss (T1%, T10%, T50%, and T95%); results obtained are reported in Table 9. TGA curves of STD and PLA1, PLA2, and PLA3 are presented in Supporting Information (S5).Table 9
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA1
257.0
296.0
320.8
337.8
PLA2
249.1
287.6
311.6
329.3
PLA3
268.8
295.5
320.2
338.4Thermal stability in comparison to STD decreases: both the beginning of degradation (T1%) and the end (T95%) occur at lower temperature. The decrease of thermal stability probably is due to both the presence of more –OH chain ends in samples with lower molecular weights in comparison to STD and the interaction with surface –OH of unmodified MMT.Thermal data of PLA nanocomposites containing silane-modified MMT are reported in Table10. TGA curves of PLA4–12 are shown in Supporting Information (S6 andS7).Table 10
Degradation data of the samples synthesized.
Sample
T
1% (°C)
T
10% (°C)
T
50% (°C)
T
95% (°C)
STD
275.2
319.4
359.2
384.7
PLA4
245.4
277.1
304.6
321.1
PLA5
289.5
339.8
382.8
400.4
PLA6
300.1
350.4
386.1
403.0
PLA7
243.5
279.2
309.6
327.0
PLA8
321.1
361.7
386.0
400.3
PLA9
323.9
348.8
375.0
400.0
PLA10
299.0
346.5
364.5
382.8
PLA11
303.2
325.4
367.0
386.0
PLA12
324.6
351.6
368.9
386.3T
1
% of PLA8 (7.5% w/w silane/MMT) is 45.9°C higher than that of STD and T10% is still very high (42.3°C higher than STD); PLA8, PLA9, PLA10, PLA11, and PLA12 show marked increases of thermal stability in the range of T1%–T95% in comparison to STD. The higher degradation temperature in comparison with PLA1, PLA2, and PLA3 can be explained considering that there are less –OH chain ends able to be involved in the backbiting ester interchange reaction and that there is no interaction of surface –OH from modified MMT due to the presence of organosilane.As a general statement, all samples with modified MMT, except for PLA4 and PLA7, show higher thermal stability in comparison to STD:T1% and T10% increase as silane content increases, indicating that thermal stability is promoted by the silane. The lower thermal stability of PLA4 and PLA7 can be explained considering that these samples have high MMT content (1% w/w) and relatively low amounts of silane on the surface. This implies that MMT platelets still have –OH moieties on the surface promoting degradation and at the same time, being better dispersed than PLA1, a high surface area in contact with the polymeric matrix. The combination of these two factors, –OH groups available on the surface and high surface area in contact with the polymer, determines lower thermal stability in comparison to both STD and other modified PLA nanocomposites.


## 3.6. Rheological Analyses

Rheological curves obtained via frequency sweep experiments on STD, PLA1, PLA2, and PLA3 are presented in Figure12.Figure 12
Rheological curves of STD and PLA1, PLA2, and PLA3.Curves have viscoelastic behaviour, with a Newtonian plateau at low shear rates and shear thinning behaviour. Zero shear viscosity values,η0 (shown in Table 11), have been calculated using Cross equation (3) passing from experimental data obtained as complex viscosity versus angular frequency to data as standard shear viscosity versus shear rate thanks to Cox-Merz rule.Table 11
Zero shear viscosity of PLA nanocomposites.
Sample
η
0 (Pa ∗ s)
STD
1.19∗ 103
PLA1
5.96∗ 103
PLA2
4.38∗ 103
PLA3
3.31∗ 103
PLA4
8.42∗ 103
PLA5
7.63∗ 103
PLA6
5.96∗ 103
PLA7
4.5∗ 103
PLA8
4.3∗ 103
PLA9
3.6∗ 103
PLA10
68.2∗ 103
PLA11
62.3∗ 103
PLA12
56.7∗ 103In Cross equation,η0 represents zero shear viscosity, η∞ is infinite-shear viscosity, γ˙ is shear rate, (1-n) is known as Cross rate constant (n is non-Newtonian behaviour index), it is dimensionless and is a measure of the degree of dependence of viscosity on shear rate in the shear thinning region, and K is known as the Cross time constant:(3)η-η∞η0-η∞=11+K2·γ˙21-n/2=11+K·γ˙1-n.Figure 12 shows that the presence of MMT consistently increases the viscosity of the melt even if SEC shows that the soluble part of PLA1–PLA3 has molecular weights far lower than those of STD. η0 is much higher and increases considerably as MMT content increases.Bearing in mind that SEC data refer only to the polymer dissolved, and therefore only to the polymer that is not chemically bonded to the nanoparticles, the high values ofη0 of unmodified samples can be due to –C=O groups of PLA that alter the normal flow of STD PLA, flowing with higher difficulty in the direction of flow and promoting the formation of a percolating network derived from the reciprocity among the strong relating sheet particles as a result of the preferential orientation of MMT layers [46].It is important to underline that, thanks to in situ synthesis, the effects of MMT on melt viscosity are greatly enhanced. Wang et al. [47] studying melt compounding of commercial PLA and MMT reported that far higher quantities of MMT (>5% w/w) were required to reach viscosity values similar to those of neat PLA and also that the inclusion of small amounts of MMT (1% w/w) lowers the complex viscosity of PLA matrix. Using “in situ” synthesis, even 0.1% w/w of MMT allows obtaining melt viscosity values far higher than those of neat PLA. When silane is present on the surface of MMT (Figure 13), the effect on melt viscosity is magnified; melt viscosity at low shears further increases, and the shear thinning behaviour is enhanced. The effect in this case may be caused by the presence of a high number of stable covalent bonds between polymer macromolecules and the silane that at low shears create a sort of network responsible for increasing viscosity [48]. At higher shears the different surface energy of unmodified MMT and PLA creates aggregation between MMT nanoparticles and generates small voids that slightly contribute to building up viscosity for unmodified samples; when silane is present, bonds between polymer and silane act as compatibilizer and prevent the aggregation of MMT and the formation of interruptions, lowering melt viscosity.Figure 13
Rheological curves of STD PLA and modified samples.This variation in melt viscosity is obtained thanks to the improved compatibility between MMT and the polymeric matrix and thanks to the quantity of MMT platelets. Besides, the increase is correlated with the structure of nanocomposites. In fact, high melt viscosities are obtained in polymer nanocomposites with fully exfoliated clay minerals with high aspect ratio that orient lamellae in the direction of flow [49], as reported in Figure 14.Figure 14
Schematic representation of MMT lamellae in PLA nanocomposites with free orientation (1) and in the direction of flow (2).


## 4. Conclusions

PLA nanocomposites were synthesized via “in situ” bulk ROP polymerization of LL-lactide with MMT. An epoxy silane was used to modify the surface of MMT and to increase the compatibility between PLA matrix and nanoparticles. Thanks to surface modification and in situ synthesis, very low amounts of nanoparticles (even 0.1% w/w MMT) are enough to get improvements previously observed with far higher quantities of clay (5% w/w or more), especially regarding melt viscosity. When MMT with no silane is used,Mn- of the polymers drops even with low quantity of mineral, but when silane is present molecular weights become even higher than those of standard PLA and dispersion of the nanoparticles in the polymeric matrix is favoured. Nanoparticles slightly enhance crystallinity of the polymers (Tc and Tcc), especially promoting melt crystallization in comparison to standard PLA and very small quantity of MMT is required when silane is present (0.1% w/w). TGA analyses show that when MMT modified with 15% w/w of organosilane is present, nanocomposites have a thermal stability (T1%) that becomes almost 50°C higher than that of standard sample.The rheological behaviours of nanocomposites show dependence both on silane and MMT content. It is important to underline that, thanks to in situ synthesis, even 0.1% w/w of MMT allows obtaining zero shear viscosity values three times higher than those of standard PLA (η0=3.31∗103 for PLA3, versus 1.19∗103 of STD sample) and that when silane is present, η0 can be even 50 times higher than that of standard PLA thanks to the reaction between the silane present on the surface of nanoparticles and polymeric chains, creating a network that increases viscosity; at higher shear rates, high quantities of silane contribute to giving a marked shear thinning behaviour, because it avoids the aggregation of nanoparticles and the formation of voids between the clay and the polymer.The overall results clearly indicate that combining the use of “in situ” synthesis that allows long contact times between mineral nanoparticles and the growing polymeric chains of PLA together with a coupling agent on the surface of MMT that can react with the polymer can result in very positive effects on many different properties of PLA nanocomposites, even with very low quantities of mineral nanoparticle, that could open new application fields for such nanocomposites. Further studies will be conducted, especially on the samples that showed the higher melt viscosity and thermal stability, to assess their potential for the production of films for packaging and disposables.



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*Source: 418418-2015-07-13.xml*