# Characterization of Physicochemical and Thermal Properties of Biofield Treated Ethyl Cellulose and Methyl Cellulose

Mahendra Kumar Trivedi, Alice Branton, Dahryn Trivedi, Gopal Nayak, Rakesh Mishra, Snehasis Jana

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## To cite this version:

Mahendra Kumar Trivedi, Alice Branton, Dahryn Trivedi, Gopal Nayak, Rakesh Mishra, et al. Characterization of Physicochemical and Thermal Properties of Biofield Treated Ethyl Cellulose and Methyl Cellulose. International Journal of Biomedical Materials Research, 2015, 3 (6), pp.83-91. hal-01503635

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# Characterization of Physicochemical and Thermal Properties of Biofield Treated Ethyl Cellulose and Methyl Cellulose

Mahendra Kumar Trivedi<fnref n="1" />, Alice Branton<fnref n="1" />, Dahryn Trivedi<fnref n="1" />, Gopal Nayak<fnref n="1" />, Rakesh Kumar Mishra<fnref n="2" />, Snehasis Jana<fnref n="2" />,*

**Email address:**
publication@trivedisrl.com (S. Jana)

**To cite this article:**
Mahendra Kumar Trivedi, Alice Branton, Dahryn Trivedi, Gopal Nayak, Rakesh Kumar Mishra, Snehasis Jana. Characterization of Physicochemical and Thermal Properties of Biofield Treated Ethyl Cellulose and Methyl Cellulose. *International Journal of Biomedical Materials Research*. Vol. 3, No. 6, 2015, pp. 83-91. doi: 10.11648/j.ijbmr.20150306.12

**Abstract:** Cellulose and its derivatives are used as potential matrices for biomaterials and tissue engineering applications. The objective of present research was to investigate the influence of biofield treatment on physical, chemical and thermal properties of ethyl cellulose (EC) and methyl cellulose (MC). The study was performed in two groups (control and treated). The control group remained as untreated, and biofield treatment was given to treated group. The biofield treated polymers are characterized by Fourier transform infrared spectroscopy (FT-IR), CHNSO analysis, X-ray diffraction study (XRD), Differential Scanning calorimetry (DSC), and thermogravimetric analysis (TGA). FT-IR analysis of treated EC showed downward shifting in C-O-C stretching peak from 1091→1066 cm⁻<fnref n="1" /> with respect to control. However, the treated MC showed upward shifting of -OH stretching (3413→3475) and downward shifting in C-O stretching (1647→1635 cm⁻<fnref n="1" />) vibrations with respect to control MC. CHNSO analysis showed substantial increase in percent hydrogen and oxygen in treated polymers with respect to control. XRD diffractogram of EC and MC affirmed the typical semi-crystalline nature. The crystallite size was substantially increased by 20.54% in treated EC with respect to control. However, the treated MC showed decrease in crystallite by 61.59% with respect to control. DSC analysis of treated EC showed minimal changes in crystallization temperature with respect to control sample. However, the treated and control MC did not show any crystallization temperature in the samples. TGA analysis of treated EC showed increase in thermal stability with respect to control. However, the TGA thermogram of treated MC showed reduction in thermal stability as compared to control. Overall, the result showed substantial alteration in physical, chemical and thermal properties of treated EC and MC.

**Keywords:** Biofield Treatment, Ethyl Cellulose, Methyl Cellulose, X-ray Diffraction Study, Differential Scanning Calorimetry, Thermogravimetric Analysis, Fourier Transform Infrared Spectroscopy

## 1. Introduction

Tissue engineering is an interdisciplinary area that uses cells, materials, engineering and life sciences toward the design and fabrication of biological substitutes that restore, support, or improve tissue or a whole organ function. Biomedical implant scaffolds are an excellent example of tissue engineering substrates composed of biodegradable polymers or inert materials coated with bioactive biomaterials which allows growth of new tissues of particular types of cells [1, 2]. Biomaterials need to be properly

modified by introducing controlled porosity, design of three-dimensional structure and surface modification to achieve better cell packing and control cell network architecture [3-8]. The biomaterial scaffold should have biodegradable and biocompatible nature. After the formation of the new tissue, polymeric scaffolds are slowly degraded into small molecular weight compounds, which was absorbed by the body or excreted out of the body [9].

In last few years hunt for new classes of biomaterials, with specific properties to be used as scaffolds for tissue engineering, has attained great interest, like cellulose, polyhydroxyalkanoates, polylactates and blends of these

<footnote n="1">¹Trivedi Global Inc., Henderson, USA</footnote>

<footnote n="2">²Trivedi Science Research Laboratory Pvt. Ltd., Bhopal, Madhya Pradesh, India</footnote>
polymers [10-15]. Recently few cellulose polymers have demonstrated excellent three-dimensional structure, water retention, high mechanical strength and biocompatibility which enable their usefulness for skin tissue regeneration [16, 17]. For example, one of the cellulose derivative bacterial cellulose has shown great potential due to its biocompatible and hygienic nature perfectly cater to the specific demand of wound tissue repair. Methyl cellulose (MC) being a derivative of cellulose family is one of the popular polymer where the -OH group are replaced by methoxyl group [18]. MC was used to prepare hydrogels by crosslinking with dialdehyde in presence of a strong acid. MC is biodegradable in nature, and popular for many biomedical applications such as drug delivery [19] and wound healing [20]. On the other hand EC is a hydrophobic polymer used as sustained release carrier; and commonly used in drug and biomedical industries for its high biodegradability and biocompatibility [21]. However, hydrophobic nature of EC and low mechanical strength of MC matrices lowers its applicability as biomaterials and tissue engineering applications. Therefore in the present work an attempt has been made to modify the properties of these cellulosic polymers (EC and MC) by biofield treatment.

It is already established that electrical currents coexist along with the magnetic field inside the human body [22]. Mr. Trivedi has the ability to harness the energy from environment or universe and can transmit into any object (living or nonliving) around this Globe. The biofield treatment has significantly enhanced the atomic and thermal properties of metals [23-26]. Additionally, the biofield treatment is known to alter the characteristics of many things in other research fields also such as, microbiology [27-29], agriculture [30-33] and biotechnology [34].

By considering above mentioned excellent results outcome from biofield treatment an attempt has been made in this work to study the physical, chemical and thermal properties of EC and MC.

## 2. Materials and Methods

Ethyl cellulose and Methyl cellulose were procured from Sigma Aldrich, USA. The sample was divided into two parts; one was kept as a control sample, while the other was subjected to Mr. Trivedi's biofield treatment and coded as treated sample. The treatment group was in sealed pack and handed over to Mr. Trivedi for biofield treatment under laboratory condition. Mr. Trivedi provided the treatment through his energy transmission process to the treated group without touching the sample. The control and treated samples of EC and MC were characterized by FT-IR, CHNSO, XRD, DSC and TGA.

### 2.1. Fourier Transform Infrared (FT-IR) Spectroscopy

The infrared spectra of control and treated EC and MC were recorded with Fourier Transform Infrared (FT-IR) Spectrometer, Perkin Elmer, USA. FT-IR spectrum was recorded in the range of 500-4000 cm⁻¹.

### 2.2. CHNSO Analysis

The control and treated EC and MC were analysed for their elemental composition (C, H, N, O, S etc.). The powdered polymer samples were subjected to CHNSO Analyser using Model Flash EA 1112 Series, Thermo Finnigan Italy.

### 2.3. X-ray Diffraction (XRD) Study

XRD of control and treated EC and MC were analysed by using Phillips Holland PW 1710 X-ray diffractometer system. The wavelength of the radiation was 1.54056 angstrom. The data was obtained in the form of 2θ versus intensity (a.u) chart. The obtained data was used for calculation of crystallite size using the following formula.

$$ \text{Crystallite size} = k\lambda/b \cos \theta \quad (1) $$

Where λ is the wavelength, k is the equipment constant (0.94) and b is full width half maximum (FWHM) of peaks.

### 2.4. Differential Scanning Calorimetry (DSC) Study

The control and treated polymers (EC and MC) were used for DSC study. The samples were analysed by using a Pyris-6 Perkin Elmer DSC on a heating rate of 10°C /min under air atmosphere.

### 2.5. Thermogravimetric Analysis (TGA)

Thermal stability of the control and treated EC and MC were analysed by using Mettler Toledo simultaneous thermogravimetric analyser and differential thermal analysis (DTA). The samples were heated from room temperature to 400°C with a heating rate of 5°C/min under air atmosphere.

## 3. Result and Discussions

### 3.1. FT-IR Spectroscopy

FT-IR spectroscopy was used to evaluate the influence of biofield treatment on chemical nature of EC and MC (Fig. 1). FT-IR of EC showed characteristic peaks at 2974 cm⁻¹ and 2869 cm⁻¹ due to C-H stretching vibration peak. The -OH stretching vibration peak was observed at 3485 cm⁻¹ in the control EC. The other important peaks at 1091, and 1373 cm⁻¹ corresponded to C-O-C stretching and C-H bending respectively [35]. The FT-IR spectrum of treated EC sample showed important peaks for -CH stretching at 2873, 2976 cm⁻¹ and -OH stretching peak was evidenced at 3485 cm⁻¹. Vibration peaks at 1066 and 1375 cm⁻¹ were mainly due to C-O-C stretch and C-H bending, respectively. The result showed that C-O-C stretch present in control EC at 1091 cm⁻¹ was shifted downward to 1066 cm⁻¹ in treated EC. Hence, it is assumed that biofield treatment may reduce the bond strength and force constant of C-O-C bond with respect to control.

FT-IR spectrum of MC showed a typical peak at -OH stretching vibration peak at 3413 cm⁻¹ [36] and C-H stretching vibration peaks at 2902 and 2835 cm⁻¹ [37]. C-O
carbonyl stretching peak was observed at 1647 cm⁻¹ and ring stretching was observed at 948 cm⁻¹ (Fig. 2). Additionally, the peak at 1373 cm⁻¹ corresponded to MC C–H bending. However, the FT-IR of biofield treated MC sample showed a downstream shifting of C-O group stretching (12 cm⁻¹) peak at 1647–1635 cm⁻¹ in the sample. Moreover, an upward

shifting in –OH group stretching 3413→3475 cm⁻¹ was observed in treated MC. The strength of bond considerably affected the energy of the covalent bonds on interactive species. Hence, it is presumed that biofield treatment may induce changes in bond strength and force constant of the treated MC with respect to control.

<figure><img src="image_3.png" /><figcaption>Fig. 1. FT-IR spectra of control and treated Ethyl cellulose.</figcaption></figure>

<figure><img src="image_4.png" /><figcaption>Fig. 2. FT-IR spectra of control and treated methyl cellulose.</figcaption></figure>

## 3.2. CHNSO Analysis

CHNSO analysis was conducted on treated and control samples of EC and MC. The CHNSO results are shown in Table 1. The result showed that the treated EC has 9.41% increase in hydrogen and 14.60% increase in oxygen element as compared to control. The treated MC also showed increase

in percentage hydrogen (8.08%) however, change in oxygen (1.46%) was not significant in treated MC. Additionally, treated EC showed decrease in 0.21 percentage carbon as compared to control polymer; and treated MC showed decrease by 4.13 of percentage carbon as compared to control. It suggests that biofield treatment may induce changes in elemental composition of the treated EC and MC.
<table><caption>Table 1. CHNSO results of ethyl cellulose and methyl cellulose.</caption><thead><tr><th>Element</th><th>Parameter</th><th>Ethyl cellulose</th><th>Methyl cellulose</th></tr></thead><tbody><tr><td rowspan="3">C</td><td>Control</td><td>56.06</td><td>48.28</td></tr><tr><td>Treated</td><td>55.95</td><td>46.28</td></tr><tr><td>% Change</td><td>-0.21</td><td>-4.13</td></tr><tr><td rowspan="3">H</td><td>Control</td><td>9.10</td><td>6.99</td></tr><tr><td>Treated</td><td>9.96</td><td>7.56</td></tr><tr><td>% Change</td><td>9.41</td><td>8.08</td></tr><tr><td rowspan="3">N</td><td>Control</td><td>0.00</td><td>0.00</td></tr><tr><td>Treated</td><td>0.00</td><td>0.00</td></tr><tr><td>% Change</td><td>-</td><td>-</td></tr><tr><td rowspan="3">O</td><td>Control</td><td>23.67</td><td>29.49</td></tr><tr><td>Treated</td><td>27.13</td><td>29.92</td></tr><tr><td>% Change</td><td>14.60</td><td>1.46</td></tr></tbody></table>

The elements present in polymers are presented in percentage.

### 3.3. X-ray Diffraction Studies

<figure><img src="image_5.png" /><figcaption>Fig. 3. XRD diffractograms of control and treated ethyl cellulose.</figcaption></figure>

X-ray diffraction studies were conducted on control (EC and MC) and treated polymer samples. XRD diffractograms of control and treated polymer samples were illustrated in Fig. 3. XRD diffractogram of control EC showed peaks at 2θ equals to 11.05° and 20.31°. However, the XRD diffractogram of treated EC showed peaks at 2θ equals to 11.04° and 22.28° (Fig. 3). This showed no significant change in XRD pattern of treated EC with respect to control. XRD diffractograms of control and treated EC showed semi-crystalline nature of the polymer. The percentage crystallite size of the treated and control EC and MC samples were computed and reported in Fig. 4. The crystallite size of the treated EC sample was increased (10.74 nm) as compared to control sample (8.91 nm). The percentage change in crystallite size was 20.54% which showed significant change

in terms of crystallite size in treated EC. It was reported previously that increase in processing temperature significantly affects the crystallite size of the materials. The increase in temperature causes decrease in dislocation density and increase in number of unit cell which ultimately causes increase in crystallite size [38, 39]. Hence, it is hypothesized that biofield treatment may provide some thermal energy to treated EC that possibly cause elevation in crystallite size of with respect to control.

X-ray diffractogram of control MC showed a broad peak at 2θ equals to 18.00°. The control MC polymer showed semi-crystalline nature with peak at 2θ equals to 20.02° (Fig. 5). This showed no change in intensity of XRD peaks of treated MC with respect to control. The control MC showed crystallite size, 83.22 nm and it was decreased to 31.96 nm in treated MC. The percentage crystallite size was decreased by -61.59%, when compared with control sample. This may be due to fracture in crystals through internal defects or sub boundaries that led to decrease in crystallite size of treated MC with respect to control.

<figure><img src="image_6.png" /><figcaption>Fig. 4. Percent change in crystallite size of treated ethyl cellulose and methyl cellulose.</figcaption></figure>

<figure><img src="image_7.png" /><figcaption>Fig. 5. XRD diffractograms of control and treated methyl cellulose.</figcaption></figure>
**3.4. Differential Scanning Calorimetry (DSC)**

DSC measures the melting temperature, glass transition temperature and crystallization nature of the polymer samples. DSC thermogram of control and treated EC samples T1, T2 were illustrated in Fig. 6. DSC thermogram of control EC showed an exothermic peak at 185.13°C which was mainly due to the crystallization temperature of the sample. The second exothermic inflexion was observed on higher temperature at 334.46°C which can be attributed to thermal degradation of the control EC (Fig. 6). The treated EC (T1) also displayed similar two exothermic peak behaviour, the first peak was due to crystallization temperature (184.76°C) and the second peak at 335.24°C corresponded to thermal degradation of the treated EC. Whereas the treated EC (T2) showed exothermic crystallization peak at 185.37°C. The second exothermic was observed at 335.08°C due to decomposition of the polymer. The result showed decrease in crystallization temperature by 0.19% in EC (T1) and it was increased by 0.12% in EC (T2). This showed slight change in crystallization temperature of treated EC (T1 and T2) samples as compared to control. It is assumed here that biofield treatment has altered the internal energy of treated EC atoms, which caused change in crystallization temperature of treated EC as compared to control.

<figure><img src="image_8.png" /><figcaption>Fig. 6. DSC thermograms of control and treated ethyl cellulose (T1 and T2).</figcaption></figure>

are presented in Fig. 7. The DSC thermogram of control and treated MC did not show crystallization peak. However, the control MC showed a broad exothermic inflexion at 301.41°C that corresponded to thermal degradation of the control. DSC thermogram of treated MC (T1) showed (Fig. 7) an exothermic transition at 301.65°C due to thermal degradation of the sample. Similarly, the treated MC (T2) sample showed slight change in thermal degradation temperature (302°C).

The enthalpy change in control and treated polymers was calculated from respective thermograms and data are presented in Table 2. The result showed that enthalpy (ΔH) of control EC was 1100 J/g whereas, the EC T1, T2 showed enthalpy value of 1020 and 841.24 J/g respectively. The percentage decrease in enthalpy for treated EC in T1 and T2 was 7.27 and 23.52% respectively as compared to control sample. However, the control MC showed a enthalpy value of 1860 J/g. After biofield treatment the enthalpy value was decreased to 1710 and 1680 J/g in treated T1 and T2 of MC, respectively. The percentage decrease in enthalpy of treated T1 and T2 of MC was 8.06 and 9.68%, respectively as compared to control. It is assumed that biofield treatment has altered the potential energy of the treated polymers that possibly led to significant change in enthalpy value as compared to control samples.
<figure><img src="image_9.png" /><figcaption>Fig. 7. DSC thermograms control and treated methyl cellulose (T1 and T2).</figcaption></figure>

<table><caption>**Table 2.** Enthalpy (ΔH) of control and treated polymers (ethyl cellulose and methyl cellulose).</caption><thead><tr><th rowspan="3">Sample</th><th colspan="2">Ethyl cellulose</th><th colspan="2">Methyl cellulose</th></tr><tr><th colspan="2">ΔH</th><th colspan="2">ΔH</th></tr><tr><th>Value (J/g)</th><th>% change</th><th>Value (J/g)</th><th>% change</th></tr></thead><tbody><tr><td>Control</td><td>1100</td><td>-</td><td>1860</td><td>-</td></tr><tr><td>T1</td><td>1020</td><td>-7.27</td><td>1710</td><td>-8.06</td></tr><tr><td>T2</td><td>841.24</td><td>-23.52</td><td>1680</td><td>-9.68</td></tr></tbody></table>

### 3.5. Thermogravimetric Analysis

Thermogravimetric analysis is a tool to investigate thermal stability, oxidation, and vaporization of the polymer samples. TGA thermogram of control and treated EC samples T1, T2 are illustrated in Fig. 8. TGA thermogram of control EC sample showed one-step thermal degradation event. The sample started to degrade thermally at around 280°C and it ended at around 380°C. The EC sample lost 80.45 % of its original weight during this event. The Derivative thermogravimetry (DTG) of control EC showed maximum decomposition temperature (Tmax) at 321°C. The thermogram of treated EC showed similar single step thermal decomposition pattern. The treated EC (T1) started to degrade at around 300°C and ended at approximately 370°C, the sample lost 57.99% of its original polymer weight. The treated EC (T1) sample showed a considerable increase in Tmax (327°C) as compared to the control sample.

<figure><img src="image_10.png" /><figcaption>Fig. 8. TGA thermograms of control and treated ethyl cellulose (T1 and T2).</figcaption></figure>
Whereas, the treated EC (T2) showed thermal degradation at around 302°C and degradation stopped at approximately 366°C. During this process T2 sample lost 59.39% of its weight. The DTG thermogram of treated EC (T2) showed Tmax at 329.09°C. The comparative evaluation of the Tmax showed increase in thermal stability of treated EC (T1 and T2) as compared to control. Szabo et al. showed that radiation treatment of poly (hexadecylthiophene) increases the thermal stability. They suggested that conformational changes in side alkyl chains of the polymer and crosslinking causes elevation in thermal stability [40]. Hence, it is presumed here that biofield treatment possibly caused conformational changes and crosslinking that increased the thermal stability.

<figure><img src="image_11.png" /><figcaption>Fig. 9. TGA thermograms of control and treated methyl cellulose (T1 and T2).</figcaption></figure>

TGA thermogram of control MC and treated MC T1 and T2 are illustrated in Fig. 9. The representative TGA thermogram of control MC showed one-step thermal degradation. The thermal degradation commenced at around 280°C and terminated at around 360°C. During this thermal process the control MC lost 59.44% of its weight. DTG thermogram of control MC showed Tmax at 317.06°C. Whereas, the thermogram of treated MC (T1) showed similar thermal degradation mechanism. The treated MC (T1) started to thermally degrade at around 290°C and it terminated at approximately 338°C. The treated MC lost 47.52% of its weight during this process. The DTG thermogram of treated T1 MC (315°C) showed decrease in Tmax value as compared to control sample (317.06°C). The treated MC (T2) started to

degrade at around 280°C and stopped at approximately 347°C. During this process the MC (T2) lost 59.78% of its polymer weight. DTG thermogram of MC (T2) also showed decrease in Tmax and it was observed at 314.71°C. This showed the decrease in thermal stability of MC T1 and T2 after biofield treatment. It is assumed that biofield treatment was unable to cause long range pattern in amorphous regions of MC, hence reduction in thermal stability.

## 4. Conclusions

The result showed significant effect of biofield treatment on physical, chemical and thermal properties of two important cellulose polymers such as EC and MC. XRD diffractogram of EC and MC (treated and control) revealed semi-crystalline nature of polymers. FT-IR spectral analysis of treated EC showed changes in C-O-C stretching with respect to control. However, the treated MC showed alteration in C-O and O-H stretching vibration peaks as compared to control. CHNSO analysis showed that biofield treatment has significantly changed the elemental composition (%H and %O) of the polymers. The treated EC showed substantial increase in crystallite size by 20.54% as compared to control. However, the treated MC showed decrease in crystallite size by 61.59% as compared to control. DSC thermogram of treated EC showed slight changes in crystallization temperature with respect to control. However, no crystallization temperature was evidenced in control and treated MC which might be due to amorphous nature of the polymer. Nevertheless, enthalpy of treated EC and MC was significantly changed after biofield treatment. TGA thermogram of treated EC showed a significant increase in Tmax which corroborates its high thermal stability. However, the treated MC showed reduction in thermal stability as compared to control. Overall, the result suggested that biofield treatment has changed the physical and thermal properties of EC and MC. Hence, it is assumed that treated EC and MC polymers could be used for biomaterial applications.

## Abbreviations

EC: Ethyl cellulose; MC: Methyl cellulose; XRD: X-ray diffraction study; TGA: Thermogravimetric analysis; DTA: Differential thermal analysis; FT-IR: Fourier transform infrared.

## Acknowledgments

We thank Dr. Cheng Dong of NLSC, Institute of Physics, and Chinese academy of Sciences for permitting us to use Powder X software for analysing XRD results. The authors would like to acknowledge the Sophisticated Analytical Instrument Facility (SAIF), Nagpur for providing the instrumental facility. The authors would like to thank Trivedi Science, Trivedi Master Wellness and Trivedi Testimonials for their support during the work.
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