Nanofibrillation of Bacterial Cellulose Using High-Pressure Homogenization and Its Films Characteristics

Heru Suryanto; Muhamad Muhajir; Bili Susilo; Yanuar Rohmat; Husni Wijaya; Abu Ansari; Uun Yanuhar

doi:10.32604/jrm.2021.015312

Heru Suryanto1,2,*, Muhamad Muhajir1, Bili Darnanto Susilo1, Yanuar Rohmat Aji Pradana1, Husni Wahyu Wijaya2,3, Abu Saad Ansari4 and Uun Yanuhar5

1Department of Mechanical Engineering, Faculty of Engineering, Universitas Negeri Malang, Malang, 65145, Indonesia
2Centre of Advanced Materials for Renewable Energy, Universitas Negeri Malang, Malang, 65145, Indonesia
3Department of Chemistry, Faculty of Mathematics and Natural Sciences, Universitas Negeri Malang, Malang, 65145, Indonesia
4Department of Chemical Engineering, Hongik University, Seoul, 04066, Korea
5Biotechnology and Waters Sciences Laboratory, Faculty of Fisheries and Marine Science, University of Brawijaya, Malang, 65145, Indonesia
*Corresponding Author: Heru Suryanto. Email: heru.suryanto.ft@um.ac.id
Received: 08 December 2020; Accepted: 01 March 2021

Globally, about 1010–1011 tons of cellulose per year is extracted from plants or plant wastes [1]. Conventional, plant-based cellulose fiber contains polysaccharides, e.g., hemicellulose and lignin, which reduces the cellulose fiber strength [2]. To overcome this issue, the plant-based cellulose fiber needs more extended and diverse nanocellulose extractions, which, will results in costs enhancement due to assorted chemical components. On the other hand, plant-based cellulose extraction requires a huge number of plants, thus lead to forest encroachment and global warming. Hence, an alternate source of cellulose is needed. The bacterial fermentation process is another prominent way to extract cellulose. Bacterial cellulose nanofibers (BCNs) production is known using coconut water as a source material [3]. Further, BCNs has successfully produced by the Gluconobacter xylinum through a static culture method using the pineapple peels extract medium [4]. Indonesia is known to be the third biggest exporter of the processed pineapples in the world, with the pineapples production capacity of 200,000 tons per year [5]. Thus, it is the great, opportunity in developing pineapple peels waste as carbon and nitrogen source for BCNs production.

BCNs, as an environmental friendly polymer resource and substitute to plant-based cellulose, is gaining attention from the world [6]. Due to BCNs biological adaptation capability. Owing to their physical and chemical properties such as high purity, well crystalline, good polymerization level, high absorbance, large water holding capacity, and high tensile strength, etc. BCNs are applied in food industry, medicines, cosmetics, acoustic diaphragm, and papermaking [7,8]. However, there is still a lot of scopes to expand further BCNs applications in various material technology sectors by engineering their properties. Diverse technological approaches are being developed to increase BCNs colloidal suspension property and fiber dispersion [9]. The production of nano-fibrillar BCNs uses a combination of mechanical, chemical, enzymatic, and chemical pre-treatments. The BCNs characteristics not only depends on the base material, but also, disintegration process [10], and treatment method [11]. Some mechanical methods to produce cellulose nanofiber are cryocrushing [12], grinding [13], High-Pressure Homogenizer (HPH) [14], and micro fluidization [15]. The enzymatic method, in combination with the shear mechanic, and HPH leads to cellulose fibrillation to nanometer dimension [16].

The HPH encourages traditional non-thermal process for emulsion stabilization and increasing texture, taste, viscosity, and color uniformity in food industries [17]. The HPH had been applied for micro-fibrillation cellulose suspension treatment in the cellulose [18,19], sugarcane bagasse, and pulp [20]. It is reported that, HPH process had applied in cellulose nanofiber isolation for decreasing the nanofiber diameter from 117 to 67 nm [21,22]. Further, ease of scaling up and operating continuously are the advantages of HPH process. The homogenizer clogging problem which is occurred due to the higher diameter of the fiber can be suppress either by increasing pressure or number of cycles in HPH process. The HPH with increasing pressure from 20 to 60 MPa at constant cycles results in the reduction of cellulose nanofiber diameter, from 94 to 60 nm [7].

The cavitation mechanism, turbulence, shearing, friction, heat, compression, velocity, and fast pressure drop initiates the HPH process [9]. The HPH process is organic solvent-free with high efficiency. Using HPH repeatedly with pressure treatment, one can generate a high fibrillation degree and high cellulose nanofibers (CNFs) [23,24]. The HPH lead to improvement in entanglement due to nano formation in the connected network structure [25]. Several groups used different characterization techniques to investigate the change in BCNs properties. HPH process on BCNs reduces dimension from microscale to nanoscale through crushing force (material particle impact strength), shear stress (material particles interaction in a space), and cavitation (extreme velocity change in the material) [22]. Microstructure information is required in the engineering of the BCNs film formation to find its structural connection towards mechanical properties and parameter in water absorbance, water release, and expansion. Therefore, this study aimed to analyze the effect of HPH cycles on BCNs film characteristics produced using a pineapple peels extract.

The synthesis of BCNs used locally isolate bacteria from Acetobacter xylinum species, provided from Microbiology Laboratory, Universitas Negeri Malang, East Java, Indonesia. The chemical sodium hydroxide (purity 98%), acetic acid/CH3COOH (purity 99%), and ammonium sulfate/(NH4)2SO4 (purity 99%) were purchased from Sigma-Aldrich (Singapore). Pineapple peel waste was obtained from a pineapple plantation at the district of Blitar, East Java, Indonesia.

Initially, the pineapple peels waste (1 kg) were cleaned, blended, pressed, and filtered to get the pineapple peel juice. Thereafter the pineapple peel juice was sterilized. 10% (wt/v) sugar, and 0.5% (v/v) ammonium sulphate (Sigma-Aldrich, Singapore) was added to pineapple peel juice, and the acidity of this culture medium was adjusted to a pH of 4.5 using acetic acid solution (Sigma-Aldrich, Singapore). A. xylinum inoculums 20% (v/v) were mixed into the medium of culture then it is fermented for ten days at 30°C. The bacterial cellulose fibers were synthesized in the form of pellicles and floated on the surface of the culture medium. The pellicles were taken and rinsed using distilled water for removing the residual medium and the other impurity. Additionally, pellicles were soaked in 1.0% NaOH solution (Sigma-Aldrich, Singapore) for 24 h then extensively rinsed with distilled water at ambient temperature until the pH of water become neutral. The purified cleaned wet pellicles were cut into smaller sizes and crushed using a high-speed blender (Fomac, ICH-DS7 model, China) at 26000 rpm for five minutes. The resulted suspension was diluted 0.5% (wt/v) by distilled water before homogenization. The suspension homogenization was carried out using HPH equipment (Berkley Scientific, AH-100D model, China) with 5, 10, 15, and 20 cycles at 150 bar pressure. The homogenized samples were poured into a glass mold (17 cm × 12.5 cm) and dried in the oven (Kirin, KBO-250RA model, Indonesia) for eight hours at 70°C. The dried samples were put inside a clipped plastic and stored in the desiccator with 58% humidity at 25°C.

Morphology Analysis. The surface morphology analysis of BCNs films was carried out by FEI, Inspect-S50 scanning electron microscope (Japan) with 30.00 kV operating voltage. Prior to morphology analysis, a thin gold layer of thickness 10 nm was coated on the BCNs films using SC7-620 Emitech sputter coater (UK). The diameter of BCNs film was the average and deviation standard measured by sofware of ImageJ 1.52a with diameter measurement of 25 times at the SEM photograph. Deviation standard was calculated using statistics function in MS.Excel program.

Structure Analysis. The structural characterization of BCNs film was examined using PAN analytical X’Pert Pro X-ray diffractometer (USA) in the range of 2θ = 10–50° with CuKα radiation (λ = 1.54 Å) at 30 mA and 40 kV. Crystalline index (CrI) is measured using the Segal formula (Eq. (1)) [26], while, the crystallite size was determined using the Scherrer formula (Eq. (2)) [22].

where: CrI represents a crystalline index, I002 is maximum peak diffraction at the crystalline plane (002) (2θ = 22– 23°), and Inon-cr is the lowest intensity value for amorphous films (the valley curve from 18° to 20°).

where: k = 0.89 is the shape factor (Scherrer’s constant), W is the full width half maximum (FWHM) in radian, θ is the Bragg angle, and λ is X-ray radiation wavelength (1.54 Å).

FTIR Analysis. Identification of the functional groups in BCNs was carried out using the Shimadzu IR Prestige-21 Fourier transform infrared (FTIR) spectrometer (Japan). For FTIR measurement, 0.1 mg BCNs was mixed with 1 mg potassium bromide (KBr) powder (high-purity infrared-grade, Sigma-Aldrich, Singapore) and pressed into a pellet. The FTIR spectrum were recorded in the range of 4000 to 400 cm–1 with a resolution of 4 cm–1.

Thickness and Surface Roughness Analysis. Both HPH and non-HPH BCNs films thickness at five different areas (15 cm × 20 cm) were measured after drying using a digital micrometer (0.0001 mm resolution, Mitutoyo Co, Japan). For roughness test, we followed the previously published method [27]. The BCNs film surface was analyzed by a portable surface tester (Surftest SJ-301 type, Mitutoyo Co, Japan) with 0.75 mN gauge precision, 0.8 mm λc profile filter, average maximum height (Rz), roughness average (Ra), and 4 mm of total length. The roughness measurement rate was 200.0 µm/cm in a horizontal direction and 5.0 µm/cm in a vertical direction.

Porosity Analysis. Surface’s porosity before and after homogenization process was analyzed by soaking BCNs films in water for four hours at 25°C. Surface porosity was measured using the Eq. (3) [28].

where: Ww is wet BCNs film weight (g), Wd is dry BCNs film weight (g), d is pure water density at room temperature (1 g/cm3), D is BCNs film thickness, and A is the surface measurement area (4 cm2).

Mechanical Properties. The mechanical property, elastic modulus and tensile strength were observed using a tensile tester (Techno Lab., Indonesia) with tension rate of 0.025 mm.s–1 and maximum load of 50 N. Tensile test of BCNs film was performed ten times with sample dimension referred to ASTM D638-V standard.

Fig. 1 shows the morphology of BCNs film before HPH process and after HPH process with various cycles. Clearly, there is a decrease in fiber diameter after HPH process compared to before HPH process (Tab. 1). Precisely, the HPH treatment implication reduces fiber diameter from 61.7 ± 36.98 nm to 46.38 ± 17.18 nm. Further, after HPH process rendered BCNs film becomes more homogenous due to the mechanical process during HPH such as centrifugal extrusion, hydraulic shear, liquid layer friction, and collision between particles.

Table 1: Fiber diameter of BCNs film after HPH process with various cycles process

We observed less reduction in fiber diameter for lower HPH cycles compared to high HPH cycles. The fiber diameter decreases from 53 to 46 nm as HPH cycles increase from 5 to 20. With increasing HPH cycles, BCNs, gradually split from its cellulose fiber and hydrogen bonds into nanofibril. Thus, HPH process with cycle variations changed microfibrils structure into the different nanofibrils structure. Additional passes contribute to the increase of surface area on the cellulose fibrils. This result was in accordance with other results research that shows after 10 passes, the diameter of most cellulose fibrils was in the range from 28 to 100 nm [29,30].

Figure 1: Surface morphology of BCNs film: (a) Non-HPH; (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

SEM of BCNs represented considerably interesting phenomena about the morphology. Fig. 1a shows BCNs film without HPH treatment. It shows porous film with many debries from culture residue. With mechanical treatment consisting of 5 and 10 passes through the HPH, there were some indications of fibrillation, the culture residue have reduce with smoother film obtained (Figs. 1b, 1c). However, with treatment of 15 to 20 passes through the HPH, these film tend to solid film with little porosity (Figs. 1d, 1c). This is caused of the expected high density of hydroxyl groups at the increased surface area make strongly interact and tend to agglomerate.

Fig. 2 depicts XRD spectra of BCNs films. The content of amorphous and crystalline constituents of BCNs films were examined from these spectra. Three characteristic diffraction peaks in all samples corresponding to crystalline plane of 1ī0, 110, and 002 [31] of cellulose were observed at 2θ value of 14.3°, 16.4°, and 22.4°, respectively. The highest intensity peak at 22.4° represents the cellulose type I [32,33].

Figure 2: XRD analysis of BCNs film (a) Non-HPH, (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

Generally, such XRD spectra having aforementioned peaks refer to cellulose Iα of BCNs film generated from pineapple peels extract. A similar result has reported earlier using sugarcane molasses medium [34] and from agro-industrial waste [35]. Clearly, the HPH process and variation in the number of cycles of HPH process reduce on the crystallite size, and CrI. However, there is no crystal form transformation as no new peak was detected in the diffraction spectra of BCNs after HPH process. With increase in HPH cycles, CrI decreased from 83% (control) to 82%, 81%, 76%, and 74% at 5, 10, 15, 20 cycles, respectively. Also, crystallite size was found to decrease from 29.2 nm (control) to 28.9 nm, 26.9 nm, 23.6 nm and 22.3 nm at 5, 10, 15, 20 cycles, respectively, as shown in Tab. 2. The reduction of crystallinity with increasing cycles might be due to surface crystallites peeling off under multiple shear and impact forces. Eyholzer et al. [36] reported that the mechanical disintegration and carboxymethylation leads to a decline in the crystallinity of nanofibers [36].

Table 2: Crystalline index and crystallite size of BCNs film after HPH with various cycles process

The effect of homogenization treatment on BCNs film chemical structure is shown in Fig. 3. The transmittance signal at ~3423 cm-1 appeared due to OH group stretching vibration from cellulose I type. The signals due to CH2 stretching and bending mode observed at ~2901 and ~1423 cm-1 respectively. Signal at ~2137 cm-1 is due to C≡C group stretching vibration of alkynes. While ~1649 cm-1 depict the O-H signal of absorbed water and ~678 cm-1 for O-H out of plane bending vibration. The signal at ~1173 cm-1 was assigned to C-O bending vibration.

Further, peak at ~1127 cm-1 is due to C-O-C asymmetric stretching from β-glycosidic link, 1091 cm-1 correspond to C-O-H stretching vibration of the sugar ring, and ~899 cm-1 for C-O-C β-glycosidic linkages between glucose units and cellulose type I [37]. Characteristic signal found at 899 cm–1 and ~1423 cm-1 confirms the samples as cellulose type I [22]. The bands of all samples in FTIR spectra are almost similar indicating no changes in the cellulose type. Additionally, the peak intensity at 3000-3500 cm–1 corresponds to hydroxyl group stretching vibration is might be an effect of interference in cellulose tissue and change in defibrillation into nanofibrils during HPH cycles. The FTIR results suggest that, though, there is a slight reduction in the transmittance peak intensity, but, the HPH process does not affect the BCNs chemical group.

Figure 3: FTIR analysis of BCNs film (a) Non-HPH, (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

The comparative roughness profile with different HPH process cycles in the forming of BCNs film is shown in Fig. 4. It can be observed that BCNs film before HPH process has a different roughness and after HPH treatment for 10 cycles BCNs film become smooth. The average roughness (Ra), height of average roughness (Rz), root mean square roughness (Rq), and thickness (t) of BCNs film with different HPH process cycles are given in Tab. 3.

The Ra for the BCNs before HPH and after 5 cycles HPH was found to be similar. Though decrease in Ra from 1.11 ± 0.06 to 0.93 ± 0.10 µm was observed with increase in HPH cycles from 5 to 10, but Ra increase back with increase in further HPH cycles. The BCNs film prepared after 10 HPH cycles is smoother compared to all. Like Ra, similar feature in Rz is observed. Rz decreases from 6.30 ± 0.32 to 5.43 ± 0.48 μm after HPH 10 cycle compared to 0 cycles, and then it increases back with increase in further HPH cycles. Rq also shows similar trend like Ra and Rz, i.e., Rq decrease after HPH and minimum Rq value was observed for 10 cycles HPH (1.15 ± 0.11 μm), but increases back for 15 and 20 cycles of HPH.

BCNs film thickness was found to decreased from 0.042 to 0.029 µm for 5 cycles HPH process compared to 0 cycle HPH. Increase in HPH cycles results in further decrease in BCNs film thickness. Though BCNs film with 20 HPH cycles depict lowest thickness, but, film prepared at 15 cycles HPH shows the lowest standard deviation (0.0016 μm).

Figure 4: Surface roughness of BCNs film: (a) Non-HPH, (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

Table 3: The average roughness (Ra), height of average roughness (Rz), root mean square roughness (Rq), and thickness (t) of BCNs film after HPH process with various cycles

Briefly, the HPH process reduces the fiber diameter of different BCNs suspension (Tab. 1). The properties of BCNs films obtained from suspension largely depend on the dispersion and size of BCNs in the suspension. The prepared BCNs films showed different roughness due to the randomly arranged BCNs film structure, twists, and bundles (Fig. 1), which is caused by rearrangement, interlacing of elementary fibrils and self-assembly of the concentrated cellulose through strong hydrogen bonds, and van der Waals forces, thus result in different morphology [38,39]. Thereby BCNs film thickness has inverse relation with HPH cycles, i.e., film thickness decreases with increase in HPH cycles and vice-versa.

The effect of HPH cycle on BCNs film porosity is shown in Fig. 5. Porosity is important to transport oxygen and diffused water into BCNs film parts. BCNs film consisted of three-dimensional nanofibers generated in the surface area having high porosity [40]. The BCNs film sample without HPH process has a porosity value 62 ± 3.9%. This porosity is similar to previous study that BC film from pellicle had porosity up to 60% [41]. After 5, 10 and 15 cycles HPH process, BCNs porosity decreases to 50 ± 1.3%, 42 ± 1.3%, 34 ± 2% and 32 ± 1.8%, respectively. A slight declined in BCNs porosity was observed after increase in HPH cycles from 15 to 20. The reducing in diameter cause the increased surface area and high density of hydroxyl groups make strongly interaction and tend to condensed. Interestingly, the number of HPH cycle controlled the porosity percentage of the formed BCNs film.

Figure 5: Porosity of BCNs film: (a) Non-HPH, (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

The impact of HPH process on tensile strength and elongation of BCNs film was examined as shown in Fig. 6. The tensile strength for non-HPH sample is 68.96 ± 9.21 MPa, and after 5, 10, 15 cycles of HPH process, the tensile strength gain values 88.21 ± 22.26, 109.15 ± 12.03, 91.79 ± 17.27, and 92.1 ± 21.83 MPa, with increased tensile strength by about 28.3%, 58.3%, 33.1%, and 33.6%, respectively. Fig. 6 also shows the rise in the sample elongations from 2.88 ± 0.01% in non-HPH to 2.50 ± 0.01% for 5, 3.20 ± 0.01% for 10, 3.28 ± 0.01% for 15, and 3.71 ± 0.01 for 20 cycles. These results show that HPH process with certain cycle variations could change the fiber network, the interaction between hydrogen bonds, and even entanglement. HPH cycles result in optimum inter-fiber interactions which lead to a network structure. These interactions influence the BCNs film tensile strength by strengthening or weakening the connectivity between fibrils on the BCNs film [42]. Lee et al. reported that hydroxypropyl cellulose film reinforced with cellulose fibrils after the 5–10 passes through the homogenizer improved significantly the strength strength and tensile modulus [30]. Similar with this results, the BCNs film produced through the HPH process with cycle variations affects the mechanical properties of the film and BCNs films after 10 cycles HPH process was found to be optimum.

Figure 6: Mechanical properties of BCNs film: (a) Non-HPH, (b) 5 cycles, (c) 10 cycles, (d) 15 cycles, and (e) 20 cycles

The present work reports the effects of HPH cycle to BCNs film properties. After different cycles levels of homogenization process, BCNs films were prepared. After HPH treatment of 20 cycles, the fiber diameter was reduced from 61.7 nm (control) to 46.38 nm; the crystalline index decreased from 83% to 74% and, the crystallite size was found to decrease from 29.2 nm to 22.3 nm. However, the HPH cycles cause a slight reduction in the transmittance peak intensity, but, it does not affect the BCNs functional group. The implementation of HPH cycles reduces the surface roughness reduced until 10 cycles with Ra of 0.93 μm. The porosity of BCNs films was reduced after higher HPH cycles. The implementation of 10 cycles HPH to BCNs was found to be optimum with a smoother surface and maximum tensile strength of 109.15 MPa. In the future, the engineered BCNs film structure could be developed into many applications in fields packaging, food industry, medicine, cosmetics, and membranes separator in the lithium-ion battery system.

Funding Statement: Author acknowledge funding support by the Universitas Negeri Malang for the PNBP research grant for PUI CAMRY with Contract No. 4.3.714/UN32.14.1/LT/2020.

Conflicts of Interest: The authors declare that they have no conflicts of interest to report regarding the present study.

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