# Synthesis, Structural Characterization, and Thermal Properties of the Poly(methylmethacrylate)/δ-FeOOH Hybrid Material: An Experimental and Theoretical Study

Authors: Silviana Corrêa; Lívia C. T. Lacerda; Maíra dos S. Pires; Marcus V. J.  Rocha; Francisco G. E. Nogueira; Adilson C. da Silva; Marcio C. Pereira; Angela D. B. de Brito; Elaine F. F. da Cunha; Teodorico C. Ramalho
Journal: Journal of Nanomaterials
 (2016)

---

## Abstract

Theδ-FeOOH/PMMA nanocomposites with 0.5 and 2.5 wt.% of δ-FeOOH were prepared by grafting 3-(trimethoxysilyl)propyl methacrylate on the surface of the iron oxyhydroxide particles. The FTIR spectra of the δ-FeOOH/PMMA nanocomposites showed that the silane monomers were covalently attached to the δ-FeOOH particles. Because of the strong interaction between the PMMA and δ-FeOOH nanoparticles, the thermal stability of the δ-FeOOH/PMMA nanocomposites was improved compared to the pure PMMA. The SEM analysis conferred the size agglomerate of particles regarding the morphology of samples. The theoretical study enabled a better understanding of the interaction of the polymer with the iron oxyhydroxide. The DFT-based calculations reinforce the radical trapping mechanism of stabilization of nanocomposites; that is, Fe3+ species might be able to accept electrons coming from the organic phase that decomposes via radical unzipping. The radical scavenge effect delays the weight loss of polymer.


---

## Body

## 1. Introduction

Nanocomposites are part of broad family of materials called organic-inorganic hybrid materials. The organic phase is comprised of polymers and the inorganic phase can be constituted of a wide variety of materials, such as metal nanoparticles, oxide nanoparticles, nanotubes, or clays [1, 2].In nanocomposites, as in other organic-inorganic hybrids, the phases are dispersed at the molecular or nanometric level, while, in microcomposites or conventional composites, inorganic fillers are dispersed at a micrometric scale. This means that, in conventional composites, the phases are immiscible [3].The use of the magnetic materials to synthesis organic-inorganic hybrids with polymer matrix has been developed to explore the physical and chemical properties. The polymers can be modeled to afford a particular architecture and arrangement of the particles, which could allow the incorporation of inorganics particles [4].Materials that can appropriately replace living tissues are called biomaterials and must present physical and biological properties consistent with these host tissues, to stimulate an adequate response. Such property characterizes biocompatibility [5].The uses of these materials in controlled release drug to bone regeneration procedures are reported in studies. In keeping with Soundrapandian and collaborators [6], polymers and ceramics are applied in nanomaterials for drug delivery in the bones. The carrier materials selected for drug delivery in bones are expected to be affordable and need exhibit predictable release characteristics, biologically and mechanically compatible with local bone tissue.The influence of the magnetic field on the controlled release of fluorescein isothiocyanate using nanoparticles of magnetite/PMMA—poly(methylmethacrylate)—and cobalt/PMMA has been studied by Urbina and collaborators [7]. The results showed a higher rate of release material with the magnetite.In this context, hybrids based on PMMA and iron oxides have been studied in recent years, especially with magnetic iron oxides. However, the magnetic property would only be guaranteed in modified polymers if there was a maximum dispersion of iron oxide on the polymeric matrix. Subsequently, PMMA was considered a suitable dispersant of magnetite nanoparticles [8].Among the magnetic iron oxides,δ-FeOOH has attracted special attention due to its stability in biochemical media [9]. δ-FeOOH is a polymorph of several common iron oxyhydroxides with a structure that is based on a hexagonal close-packed oxygen lattice similar to that of hematite (α-Fe2O3) with iron occupying half of the available octahedral interstices [9]. Due to its superparamagnetic properties [10], δ-FeOOH is a potentially interesting material to be used in modern medicine. Despite its great importance, surprisingly little detailed computational and experimental work on this subject has appeared.Thus, the current work aims to developδ-FeOOH/PMMA hybrids, characterizing their structure, morphology, and thermal properties by using several experimental techniques as well as to perform theoretical investigations involving structural and electronic parameters.


## 2. Materials and Methods

### 2.1. Synthesis of PMMA/δ-FeOOH Films

The synthesis ofδ-FeOOH was carried out according to the modified procedure described by Chagas and collaborators [10]. It consists of precipitating Fe2+ alcoholic solution with NaOH followed by fast oxidation with H2O2, enabling the direct attainment of the δ-FeOOH.The 3-(trimethoxysilyl)propyl methacrylate (Aldrich) (TMSM) was used to graft the nanoparticles. For that 500 mg of dried nanoparticles was dispersed in a solution of 1 mL of TMSM and 2 mL of tetrahydrofuran (THF, Aldrich). This mixture was kept in an ultrasound bath for 24 hours at 55°C. The nanoparticles were washed three times with toluene (Aldrich) and recuperated by centrifugation (7000 g for 30 min); then they were dried for 24 hours at 50°C.Finally, the grafted nanoparticles were dispersed by ultrasound during 4 hours in 2 mL of THF and mixed with 2.015 mL of methylmethacrylate (Aldrich) (MMA), 2 mL of THF, and 5 mg of BPO (Benzoyl Peroxide). This mixture was then kept under ultrasound for 2 hours. Polymerization of MMA was made by keeping the samples for 12 hours at 70°C. The nanocomposites were deposited on Teflon™ sheets and then dried under air atmosphere for 24 hours at room temperature. The resulting free (not supported) films were dried for 12 hours at 100°C.


### 2.2. Characterization

The nanostructures of the hybrid films were characterized by Fourier transform infrared (FTIR) spectroscopy using Spectrum 2000 PerkinElmer. FTIR measurements were performed in attenuated total reflexion (ATR) mode, thus obtaining vibrational absorption spectra over a spectral range of 4000–400 cm−1.The crystalline structure was analyzed by X-ray powder diffraction (XRD). Data were obtained using X’Pert Pro multipurpose X-ray diffraction (MPD) system employing Cu Kα radiation (λ = 0.154 nm) operated at 40 mA and 45 kV.Scanning electron microscopy (SEM) was performed on samples using LEO VP 435 scanning electron microscope operating at 20 kV.The thermogravimetric analyses were performed in triplicate using a Mettler Toledo equipment (TG/DSC1) Star System, using 10 mg of sample, in the temperatures of 25 to 1000°C with a heating rate of 10°C min−1 in a synthetic air atmosphere.


### 2.3. Computational Details

All calculations were performed with DFT (Density Functional Theory) method using the ADF-BAND 2009.01 program  [11, 12]. The performance for computing the geometries has been done by the PBE density functional. In conjunction with PBE density functional, the TZP basis set has been used, which is a large uncontracted set of Slater-type orbitals containing diffuse functions, which is of triple-ζ quality and has been improved with one set of polarization function: 3d on carbon and silicon, 4f on iron, and 2p on hydrogen. The frozen core approximation was used in the inner cores of O (1s) and Fe (1s2s2p) atoms.Theδ-FeOOH structure was built using the parameters based on previous studies [13], with space group P-3m1. It has only Fe3+ atoms at the octahedral sites “0, 0, and 0” and “0, 0, and 1/2.” The positions of O and H atoms are defined by their coordinates “1/3, 2/3, and 0.2468” and “1/3, 2/3, and 0.51,” the lattices parameters a=2.946 Å and c=4.552 Å For the potential surface energy calculation, were varied the PMMA angles of 80 to 200° about the iron oxyhydroxide.


## 2.1. Synthesis of PMMA/δ-FeOOH Films

The synthesis ofδ-FeOOH was carried out according to the modified procedure described by Chagas and collaborators [10]. It consists of precipitating Fe2+ alcoholic solution with NaOH followed by fast oxidation with H2O2, enabling the direct attainment of the δ-FeOOH.The 3-(trimethoxysilyl)propyl methacrylate (Aldrich) (TMSM) was used to graft the nanoparticles. For that 500 mg of dried nanoparticles was dispersed in a solution of 1 mL of TMSM and 2 mL of tetrahydrofuran (THF, Aldrich). This mixture was kept in an ultrasound bath for 24 hours at 55°C. The nanoparticles were washed three times with toluene (Aldrich) and recuperated by centrifugation (7000 g for 30 min); then they were dried for 24 hours at 50°C.Finally, the grafted nanoparticles were dispersed by ultrasound during 4 hours in 2 mL of THF and mixed with 2.015 mL of methylmethacrylate (Aldrich) (MMA), 2 mL of THF, and 5 mg of BPO (Benzoyl Peroxide). This mixture was then kept under ultrasound for 2 hours. Polymerization of MMA was made by keeping the samples for 12 hours at 70°C. The nanocomposites were deposited on Teflon™ sheets and then dried under air atmosphere for 24 hours at room temperature. The resulting free (not supported) films were dried for 12 hours at 100°C.


## 2.2. Characterization

The nanostructures of the hybrid films were characterized by Fourier transform infrared (FTIR) spectroscopy using Spectrum 2000 PerkinElmer. FTIR measurements were performed in attenuated total reflexion (ATR) mode, thus obtaining vibrational absorption spectra over a spectral range of 4000–400 cm−1.The crystalline structure was analyzed by X-ray powder diffraction (XRD). Data were obtained using X’Pert Pro multipurpose X-ray diffraction (MPD) system employing Cu Kα radiation (λ = 0.154 nm) operated at 40 mA and 45 kV.Scanning electron microscopy (SEM) was performed on samples using LEO VP 435 scanning electron microscope operating at 20 kV.The thermogravimetric analyses were performed in triplicate using a Mettler Toledo equipment (TG/DSC1) Star System, using 10 mg of sample, in the temperatures of 25 to 1000°C with a heating rate of 10°C min−1 in a synthetic air atmosphere.


## 2.3. Computational Details

All calculations were performed with DFT (Density Functional Theory) method using the ADF-BAND 2009.01 program  [11, 12]. The performance for computing the geometries has been done by the PBE density functional. In conjunction with PBE density functional, the TZP basis set has been used, which is a large uncontracted set of Slater-type orbitals containing diffuse functions, which is of triple-ζ quality and has been improved with one set of polarization function: 3d on carbon and silicon, 4f on iron, and 2p on hydrogen. The frozen core approximation was used in the inner cores of O (1s) and Fe (1s2s2p) atoms.Theδ-FeOOH structure was built using the parameters based on previous studies [13], with space group P-3m1. It has only Fe3+ atoms at the octahedral sites “0, 0, and 0” and “0, 0, and 1/2.” The positions of O and H atoms are defined by their coordinates “1/3, 2/3, and 0.2468” and “1/3, 2/3, and 0.51,” the lattices parameters a=2.946 Å and c=4.552 Å For the potential surface energy calculation, were varied the PMMA angles of 80 to 200° about the iron oxyhydroxide.


## 3. Results and Discussion

### 3.1. Structural Characterization

In the present workδ-FeOOH and the grafted δ-FeOOH/TMSM samples were characterized with ATR infrared spectroscopy. The obtained results are summarized in Figure 1. The ATR spectrum of δ-FeOOH (Figure 1) shows a very strong and broad band at 3265 cm−1 that can be associated with the stretching modes of molecules water, present on its surface. The two bands at 1096 cm−1 and 908 cm−1 correspond to Fe-O-H bending vibrations [13]. The most remarkable band is located at 1701 cm−1 and it corresponds to carbonyl (C=O) vibrations on TMSM structure. The infrared spectrum of functionalized δ-FeOOH showed a band centered at 1096 cm−1, which can be attributed to Si-O-Fe vibrations [14, 15]. It suggests that the silane monomers were covalently bonded to δ-FeOOH particles. It should be kept in mind, however, that the infrared bands are attributed to Fe-O-H bending vibrations in the same region. Despite this feature, the functionalization occurs in the formation of the Si-O-Fe bonding, because the Fe-O-H bending vibration at 908 cm−1 disappears in δ-FeOOH/TMSM infrared spectrum. Probably, one or two Si-OCH3 groups are broken after functionalization reaction. Figure 2 represents the atomic model of δ-FeOOH/PMMA hybrid material.Figure 1
FTIR spectra ofδ-FeOOH and grafted δ-FeOOH.Figure 2
Atomic model of aδ-FeOOH nanocrystal embedded in the PMMA.The loss of two or three methyl groups of TMSM led to a new chemical bond between oxygen atoms fromδ-FeOOH and silicon. The nucleophilic substitution of Fe-OH into Si(OCH3) can be described as(1)Fe-OH+Si-OCH3⟶Fe-O-Si+CH3OHIn the study of Pereira and collaborators [9], there were found peaks in the X-ray diffraction pattern “100,” “101,” “102,” and “110” characteristic of δ-FeOOH. The lattice parameters can be indexed on a hexagonal lattice with a=2.946 Å and c=4.552 Å.The XRD patterns were recorded for the nanoparticles after grafting with TMSM molecules. Figures3(a) and 3(b) reveal the presence of peaks 2θ = 36°, 56°, and 63°, approximately, corresponding to the “100,” “102,” and “110,” to the grafted δ-FeOOH 0.5 wt.% and 2.5 wt.%.Figure 3
Powder X-ray diffraction pattern of graftedδ-FeOOH 0.5 wt.% (a) and 2.5 wt.% (b) sample.
(a)
Polymer 0.5 wt.% FeOOH
(b)
Polymer 2.5 wt.% FeOOHThe XRD showed bands characteristic of PMMA such as in the study of Shobhana and the peaks ofδ-FeOOH [16] confirming the presence of PMMA and δ-FeOOH in this material. Because the main peaks are represented in both XRD patterns, in the second (Figure 3(b)), the peak intensity is smaller; it can be interpreted by the fact that sample has a higher percentage of feroxyhyte 2.5 wt.%. Already in Figure 3(a), the intensity is large for the grafted δ-FeOOH 0.5 wt.%.Figures4(a) and 4(b) show the images obtained by SEM of surface and cross section fractured under liquid nitrogen of hybrids with 2.5 wt.% of δ-FeOOH nanoparticles, respectively.Figure 4
SEM micrographs of PMMA/δ-FeOOH hybrid with (a) 0.5 and (b) 2.5 wt.% of δ-FeOOH.
(a)
(b)A general analysis of the micrographs of all samples shows agglomerates of different sizes and with irregular blocks formats throughout the film. The average size of the agglomerates was larger than 1μm to 30 μm, indicating a broad size distribution.


### 3.2. Thermal Properties

The thermal stabilities of the obtained hybrid materials were determined by thermogravimetric analysis (TGA) and differential thermogravimetric (DTA).Figures5 and 6 display the TG and DTA curves of PMMA, δ-FeOOH grafted with TMSM, and δ-FeOOH/PMMA hybrid. These TG and DTA curves indicate that the neat δ-FeOOH and δ-FeOOH/TMSM sample weight loss occurs in two and three distinct steps, respectively. For both of the materials, the first step of weight loss can be attributed to the free water in the powder. For neat δ-FeOOH particles, about 11% weight loss is observed at 273°C, which is due to the crystal transition of δ-FeOOH to hematite [13].Figure 5
Thermogravimetric curves of pure PMMA and PMMA with differentδ-FeOOH contents.Figure 6
Differential thermogravimetric (DTA) curves ofδ-FeOOH, Polymer, and δ-FeOOH/PMMA hybrid 0.5 and 2.5 wt.%.By analyzing theδ-FeOOH grafted with TMSM, after the first step attributed to the free water in the powder, it can be related to another weight loss at 289°C, which is due to the silane groups grafted on the iron oxyhydroxide surface. The grafting process shifted the second decomposition step of δ-FeOOH at 340°C to higher values, suggesting higher thermal stability.Concerning the thermal decomposition of PMMA, this can take place in three stages: the first step between 130 and 260°C is related to the decomposition starting at the head-to-head chain segments. The second step between 260 and 370°C is attributed to first unzipping starting at unsaturated polymer end chains, and the third step between 370 and 500°C corresponds to the random joining of polymeric chains [17, 18].The DTA curves shown in Figure6 indicate that the starting temperature of the second decomposition step is shifted to higher values for increasing δ-FeOOH loading, while the end of this step is only slightly affected by δ-FeOOH content. This implies that the increasing amount of δ-FeOOH nanoparticles delays the beginning of polymer unzipping. However, during the decomposition the δ-FeOOH nanoparticles confer suppressing effect that seems to be independent of their loading in the nanocomposite, at least within the 0.5 to 2.5 wt.% range presented in this study.We can also notice, in Figure6, that the maximum degradation rate of PMMA occurs at 293°C, while increasing δ-FeOOH loading this maximum shifts toward higher temperatures, from T = 378°C for δ-FeOOH 0.5 wt.% up to 389°C for δ-FeOOH 2.5 wt.%.The radical trapping effect might be the responsible for the thermal stability improvement observed for the increasing amount ofδ-FeOOH nanoparticles. This effect was recently demonstrated for inorganic hybrids with PMMA [19–22]. Therefore the thermal improvement reported above may take place due to a similar effect that may be undergoing in the presence of δ-FeOOH, which acts as radical trappers and accepts the unpaired electron from the radical polymer chain thus stopping or retarding the unzipping.


#### 3.2.1.δ-FeOOH Bulk

For study, theoretical calculations with the relativistic effects DFT/ZORA/PBE method of the surface ofδ-FeOOH before the functionalization process were performed. From the planes examined, “100,” “101,” “102,” and “110,” the more stable one was “100.”In the density of states (DOS) graphs, the valence band located in the region of the oxygen 2p and the conduction band situated in the region of the iron 3d (Figure7) indicate an electron transfer from O2− anions to Fe3+ cations.Figure 7
Densities of states (DOS) of octahedral Fe and O in the bulkδ-FeOOH.Figure8 shows areas with high and low electron density in green and red color, respectively. The valence charge density is higher in the volumes close to O atoms. These are preferential regions for nucleophilic or electrophilic substitution, where Fe-OH reacts with Si-OCH3 to originate Fe-O-Si bonds.Figure 8
Electrostatic surface contours ofδ-FeOOH bulk. Red and green indicate volumes of low electron density and high electron density, respectively. Red = oxygen, white = hydrogen, and pink = iron.


#### 3.2.2. PMMA/δ-FeOOH

The potential energy surface varying the PMMA angle in relation to the oxide surface by angles (I) Si-C-C-C and (II) C-C-O-C from 80 to 200° has been determined. This feature allowed us to evaluate the probable conformation of the monomer of the polymeric matrix close to the surface of feroxyhyte nanoparticles. Our results plotted in Figure9 indicate that the minimum energy or most stable conformation of PMMA molecule on the δ-FeOOH surface lies in the range of 155–130°.Figure 9
Surface potential energy ofδ-FeOOH/PMMA as a function of the (I) Si-C-C-C and (II) C-O-C-C angles. 3D surface: 1′ versus 2′ versus energy. Energy = distance weighted least squares.Theδ-FeOOH surface interferes in the PMMA angles so that the system stability increases while angles I and II reduce. This phenomenon can be explained by attractive electrostatic interactions, either between the positive regions of the PMMA and the surface oxygen or between π-electrons of the end of the molecule and the empty orbital of iron atoms present on the surface. This trend prevailed while the electronic effects were greater than the steric effects.


## 3.1. Structural Characterization

In the present workδ-FeOOH and the grafted δ-FeOOH/TMSM samples were characterized with ATR infrared spectroscopy. The obtained results are summarized in Figure 1. The ATR spectrum of δ-FeOOH (Figure 1) shows a very strong and broad band at 3265 cm−1 that can be associated with the stretching modes of molecules water, present on its surface. The two bands at 1096 cm−1 and 908 cm−1 correspond to Fe-O-H bending vibrations [13]. The most remarkable band is located at 1701 cm−1 and it corresponds to carbonyl (C=O) vibrations on TMSM structure. The infrared spectrum of functionalized δ-FeOOH showed a band centered at 1096 cm−1, which can be attributed to Si-O-Fe vibrations [14, 15]. It suggests that the silane monomers were covalently bonded to δ-FeOOH particles. It should be kept in mind, however, that the infrared bands are attributed to Fe-O-H bending vibrations in the same region. Despite this feature, the functionalization occurs in the formation of the Si-O-Fe bonding, because the Fe-O-H bending vibration at 908 cm−1 disappears in δ-FeOOH/TMSM infrared spectrum. Probably, one or two Si-OCH3 groups are broken after functionalization reaction. Figure 2 represents the atomic model of δ-FeOOH/PMMA hybrid material.Figure 1
FTIR spectra ofδ-FeOOH and grafted δ-FeOOH.Figure 2
Atomic model of aδ-FeOOH nanocrystal embedded in the PMMA.The loss of two or three methyl groups of TMSM led to a new chemical bond between oxygen atoms fromδ-FeOOH and silicon. The nucleophilic substitution of Fe-OH into Si(OCH3) can be described as(1)Fe-OH+Si-OCH3⟶Fe-O-Si+CH3OHIn the study of Pereira and collaborators [9], there were found peaks in the X-ray diffraction pattern “100,” “101,” “102,” and “110” characteristic of δ-FeOOH. The lattice parameters can be indexed on a hexagonal lattice with a=2.946 Å and c=4.552 Å.The XRD patterns were recorded for the nanoparticles after grafting with TMSM molecules. Figures3(a) and 3(b) reveal the presence of peaks 2θ = 36°, 56°, and 63°, approximately, corresponding to the “100,” “102,” and “110,” to the grafted δ-FeOOH 0.5 wt.% and 2.5 wt.%.Figure 3
Powder X-ray diffraction pattern of graftedδ-FeOOH 0.5 wt.% (a) and 2.5 wt.% (b) sample.
(a)
Polymer 0.5 wt.% FeOOH
(b)
Polymer 2.5 wt.% FeOOHThe XRD showed bands characteristic of PMMA such as in the study of Shobhana and the peaks ofδ-FeOOH [16] confirming the presence of PMMA and δ-FeOOH in this material. Because the main peaks are represented in both XRD patterns, in the second (Figure 3(b)), the peak intensity is smaller; it can be interpreted by the fact that sample has a higher percentage of feroxyhyte 2.5 wt.%. Already in Figure 3(a), the intensity is large for the grafted δ-FeOOH 0.5 wt.%.Figures4(a) and 4(b) show the images obtained by SEM of surface and cross section fractured under liquid nitrogen of hybrids with 2.5 wt.% of δ-FeOOH nanoparticles, respectively.Figure 4
SEM micrographs of PMMA/δ-FeOOH hybrid with (a) 0.5 and (b) 2.5 wt.% of δ-FeOOH.
(a)
(b)A general analysis of the micrographs of all samples shows agglomerates of different sizes and with irregular blocks formats throughout the film. The average size of the agglomerates was larger than 1μm to 30 μm, indicating a broad size distribution.


## 3.2. Thermal Properties

The thermal stabilities of the obtained hybrid materials were determined by thermogravimetric analysis (TGA) and differential thermogravimetric (DTA).Figures5 and 6 display the TG and DTA curves of PMMA, δ-FeOOH grafted with TMSM, and δ-FeOOH/PMMA hybrid. These TG and DTA curves indicate that the neat δ-FeOOH and δ-FeOOH/TMSM sample weight loss occurs in two and three distinct steps, respectively. For both of the materials, the first step of weight loss can be attributed to the free water in the powder. For neat δ-FeOOH particles, about 11% weight loss is observed at 273°C, which is due to the crystal transition of δ-FeOOH to hematite [13].Figure 5
Thermogravimetric curves of pure PMMA and PMMA with differentδ-FeOOH contents.Figure 6
Differential thermogravimetric (DTA) curves ofδ-FeOOH, Polymer, and δ-FeOOH/PMMA hybrid 0.5 and 2.5 wt.%.By analyzing theδ-FeOOH grafted with TMSM, after the first step attributed to the free water in the powder, it can be related to another weight loss at 289°C, which is due to the silane groups grafted on the iron oxyhydroxide surface. The grafting process shifted the second decomposition step of δ-FeOOH at 340°C to higher values, suggesting higher thermal stability.Concerning the thermal decomposition of PMMA, this can take place in three stages: the first step between 130 and 260°C is related to the decomposition starting at the head-to-head chain segments. The second step between 260 and 370°C is attributed to first unzipping starting at unsaturated polymer end chains, and the third step between 370 and 500°C corresponds to the random joining of polymeric chains [17, 18].The DTA curves shown in Figure6 indicate that the starting temperature of the second decomposition step is shifted to higher values for increasing δ-FeOOH loading, while the end of this step is only slightly affected by δ-FeOOH content. This implies that the increasing amount of δ-FeOOH nanoparticles delays the beginning of polymer unzipping. However, during the decomposition the δ-FeOOH nanoparticles confer suppressing effect that seems to be independent of their loading in the nanocomposite, at least within the 0.5 to 2.5 wt.% range presented in this study.We can also notice, in Figure6, that the maximum degradation rate of PMMA occurs at 293°C, while increasing δ-FeOOH loading this maximum shifts toward higher temperatures, from T = 378°C for δ-FeOOH 0.5 wt.% up to 389°C for δ-FeOOH 2.5 wt.%.The radical trapping effect might be the responsible for the thermal stability improvement observed for the increasing amount ofδ-FeOOH nanoparticles. This effect was recently demonstrated for inorganic hybrids with PMMA [19–22]. Therefore the thermal improvement reported above may take place due to a similar effect that may be undergoing in the presence of δ-FeOOH, which acts as radical trappers and accepts the unpaired electron from the radical polymer chain thus stopping or retarding the unzipping.


### 3.2.1.δ-FeOOH Bulk

For study, theoretical calculations with the relativistic effects DFT/ZORA/PBE method of the surface ofδ-FeOOH before the functionalization process were performed. From the planes examined, “100,” “101,” “102,” and “110,” the more stable one was “100.”In the density of states (DOS) graphs, the valence band located in the region of the oxygen 2p and the conduction band situated in the region of the iron 3d (Figure7) indicate an electron transfer from O2− anions to Fe3+ cations.Figure 7
Densities of states (DOS) of octahedral Fe and O in the bulkδ-FeOOH.Figure8 shows areas with high and low electron density in green and red color, respectively. The valence charge density is higher in the volumes close to O atoms. These are preferential regions for nucleophilic or electrophilic substitution, where Fe-OH reacts with Si-OCH3 to originate Fe-O-Si bonds.Figure 8
Electrostatic surface contours ofδ-FeOOH bulk. Red and green indicate volumes of low electron density and high electron density, respectively. Red = oxygen, white = hydrogen, and pink = iron.


### 3.2.2. PMMA/δ-FeOOH

The potential energy surface varying the PMMA angle in relation to the oxide surface by angles (I) Si-C-C-C and (II) C-C-O-C from 80 to 200° has been determined. This feature allowed us to evaluate the probable conformation of the monomer of the polymeric matrix close to the surface of feroxyhyte nanoparticles. Our results plotted in Figure9 indicate that the minimum energy or most stable conformation of PMMA molecule on the δ-FeOOH surface lies in the range of 155–130°.Figure 9
Surface potential energy ofδ-FeOOH/PMMA as a function of the (I) Si-C-C-C and (II) C-O-C-C angles. 3D surface: 1′ versus 2′ versus energy. Energy = distance weighted least squares.Theδ-FeOOH surface interferes in the PMMA angles so that the system stability increases while angles I and II reduce. This phenomenon can be explained by attractive electrostatic interactions, either between the positive regions of the PMMA and the surface oxygen or between π-electrons of the end of the molecule and the empty orbital of iron atoms present on the surface. This trend prevailed while the electronic effects were greater than the steric effects.


## 3.2.1.δ-FeOOH Bulk

For study, theoretical calculations with the relativistic effects DFT/ZORA/PBE method of the surface ofδ-FeOOH before the functionalization process were performed. From the planes examined, “100,” “101,” “102,” and “110,” the more stable one was “100.”In the density of states (DOS) graphs, the valence band located in the region of the oxygen 2p and the conduction band situated in the region of the iron 3d (Figure7) indicate an electron transfer from O2− anions to Fe3+ cations.Figure 7
Densities of states (DOS) of octahedral Fe and O in the bulkδ-FeOOH.Figure8 shows areas with high and low electron density in green and red color, respectively. The valence charge density is higher in the volumes close to O atoms. These are preferential regions for nucleophilic or electrophilic substitution, where Fe-OH reacts with Si-OCH3 to originate Fe-O-Si bonds.Figure 8
Electrostatic surface contours ofδ-FeOOH bulk. Red and green indicate volumes of low electron density and high electron density, respectively. Red = oxygen, white = hydrogen, and pink = iron.


## 3.2.2. PMMA/δ-FeOOH

The potential energy surface varying the PMMA angle in relation to the oxide surface by angles (I) Si-C-C-C and (II) C-C-O-C from 80 to 200° has been determined. This feature allowed us to evaluate the probable conformation of the monomer of the polymeric matrix close to the surface of feroxyhyte nanoparticles. Our results plotted in Figure9 indicate that the minimum energy or most stable conformation of PMMA molecule on the δ-FeOOH surface lies in the range of 155–130°.Figure 9
Surface potential energy ofδ-FeOOH/PMMA as a function of the (I) Si-C-C-C and (II) C-O-C-C angles. 3D surface: 1′ versus 2′ versus energy. Energy = distance weighted least squares.Theδ-FeOOH surface interferes in the PMMA angles so that the system stability increases while angles I and II reduce. This phenomenon can be explained by attractive electrostatic interactions, either between the positive regions of the PMMA and the surface oxygen or between π-electrons of the end of the molecule and the empty orbital of iron atoms present on the surface. This trend prevailed while the electronic effects were greater than the steric effects.


## 4. Conclusions

The hybrid nanocompositesδ-FeOOH/PMMA were successfully prepared. The results of SEM confirmed the dispersion of δ-FeOOH particles in the polymer matrix.The TG analysis showed that the thermal stability ofδ-FeOOH/PMMA nanocomposites is higher than that of pure PMMA. This trend became more evident by increasing the iron concentration.The results of FTIR indicate the existence of covalent bonding between silane monomers and atoms located on the surface of theδ-FeOOH nanoparticles. This was confirmed by surface charge density map, which clearly showed the presence of regions likely to perform this type of interaction.In general, the computational studies, coupled with experimental characterizations, allowed a better understanding of the morphology, structure, and electronic properties of hybridδ-FeOOH/PMMA.



---

*Source: 2462135-2016-02-08.xml*