- freely available
Int. J. Mol. Sci. 2014, 15(4), 6423-6440; doi:10.3390/ijms15046423
Abstract: Nanofibrillated cellulose (NFC) films have potential as oxygen barriers for, e.g., food packaging applications, but their use is limited by their hygroscopic characteristics. The three-dimensional microstructure of NFC films made of Pinus radiata (Radiata Pine) kraft pulp fibres has been assessed in this study, considering the structural development as a function of relative humidity (RH). The surface roughness, micro-porosity, thickness and their correlations were analyzed using X-ray microtomography (X–μCT) and computerized image analysis. The results are compared to those from scanning electron microscopy and laser profilometry. Based on a series of films having varying amounts of 2,2,6,6-tetramethylpiperidinyl-1-oxyl (TEMPO)-mediated oxidated nanofibrils, it was demonstrated that X–μCT is suitable for assessing the surface and bulk 3D microstructure of the cellulose films. Additionally, one of the series was assessed at varying humidity levels, using the non-destructive capabilities of X–μCT and a newly developed humidity chamber for in-situ characterization. The oxygen transmission rate (OTR) of the films (20 g/m2) was below 3.7mLm−2 day−1 at humidity levels below 60% RH. However, the OTR increased considerably to 12.4mLm−2 day−1 when the humidity level increased to 80% RH. The increase in OTR was attributed to a change of the film porosity, which was reflected as an increase in local thickness. Hence, the characterization techniques applied in this study shed more light on the structures of NFC films and how they are affected by varying humidity levels. It was demonstrated that in increasing relative humidity the films swelled and the oxygen barrier properties decreased.
1.1. Nanofibrillated Cellulose
Vascular plant cell walls are composed of elementary fibrils which have been reported to have a width of 3.5nm [1,2]. The fibrils are composed of 36 β-1,4-glucan chains, which are synthesised by rosette complexes, i.e., cellulose synthase proteins in the plasma membrane [3,4]. In wood, the fibrils are arranged differently in the different layers which compose the fibre wall, i.e., the primary wall (P) and the secondary wall layers (S1, S2 and S3).
Nanofibrillated cellulose (NFC) refers to the material that is produced based on the disintegration of the fibre wall into a major fraction of individualized elementary fibrils and their aggregates. Chemical pretreatments such as TEMPO mediated oxidation yield homogenous fibrillated materials with typical fibril diameters less than 20nm (see also [5–7]). NFC can be produced from various green resources, such as wood, agricultural residues and annual crops [6–10], and is thus renewable and biodegradable. In addition, the material has several advantages from a mechanical, optical and structural point of view and has been proposed for several applications [6,11–16]. Films made of NFC have been reported to be strong (tensile strength > 200MPa, ) and with good oxygen barrier properties. For a good overview of oxygen permeability of NFC materials see , where values between 5 and 0.1mLμmm−2 day−1 kPa−1 have been reported (measured at 23 °C and 50% relative humidity), and also [13,19–22]. Additionally, NFC films have high translucency (>90% according to [19,21]), making them a suitable material for, e.g., food packaging applications. However, neat NFC films are hygroscopic, i.e., the humidity reduces the oxygen barrier properties. An increase of the oxygen transmission rate (OTR) has been reported for NFC films when increasing the relative humidity (RH) (e.g., ). However, to our knowledge no direct assessment of the three-dimensional structural changes as a function of relative humidity has been reported.
1.2. Structural Quantification
It is important to perform an adequate quantification of the structure of NFC materials. From a structural point of view, thickness is an important property, which is utilized for estimating the tensile strength, density and oxygen permeability of NFC films. Additionally, multi-scale assessments of the surface roughness can yield detailed information of the surface structural properties of NFC films, which are affected by residual fibres and morphology of fibrils . Structural characterisation tools such as scanning electron microscopy (SEM), laser profilometry (LP), atomic force microscopy (AFM) and transmission electron microscopy (TEM) have been successfully applied for quantification of NFC-based structures [7,8,19,23–29].
X-ray microtomography (X–μCT) is a non-destructive method to obtain the three-dimensional structure of a given sample . Complemented by image analysis, it can be used to estimate, e.g., the thickness, roughness and micro-porosity of NFC films in a single measurement. Additionally, as the method is non-destructive, the same sample can be measured multiple times in varying environmental conditions. Thus it is relatively easy to obtain structural parameters as a function of, e.g., temperature or relative humidity.
It is the intention of this work to introduce the X–μCT characterization tool in combination with an in-situ equipment, which can be applied for assessing structural changes of hygroscopic materials such as NFC films. The suitability of these novel techniques is exemplified by performing a characterisation of the microstructure of NFC films, which have varying composition of TEMPO-mediated NFC as indicated in Table 1.
2. Results and Discussion
2.1. Structural Quantification
As an example of the X–μCT images, a three-dimensional visualization of film T0 is exemplified in Figure 1. Based on visual inspection, the film surface is very rough and the micro-porosity (pores of size scale ≳ 1 μm) contributes significantly to the total volume of the film. Figure 2 shows cross-sectional X–μCT slices of films T0 and T100. Based on the image, the mean thicknesses of the two films seem to be approximately equal, but the surface roughness of the T0 film is higher, especially in the top surface. In the T0 film there are also some pores that are not visible in the T100 sample. This observation is confirmed by the results shown in Figures 3 and 4, where the thickness and roughness of each individual film is presented. The thickness and roughness quantified by X–μCT are also compared with the corresponding results from SEM and LP respectively, which give similar estimates. It is worth to notice the large difference between the apparent thickness and the intrinsic thicknesses measured using SEM and X–μCT. As confirmed in this study, the thickness can be overestimated up to roughly 100%, depending on the NFC material and the device applied for thickness measurements (see also ).
The surface topography, thickness and micro-porosity maps for film T0 are presented in Figure 5. Based on the maps, most of the thickness variations and roughness seems to be caused by residual fibres that form unevenness in the film surface. High correlation between top surface topography maps and thickness maps (Figure 6) shows that for all the films the top surface roughness is mostly related to variations in thickness. The roughness at the bottom surface, i.e., the one that faced the petri dish surface, is low (Figure 4) and only weakly correlated with thickness (Figure 6). Recently it has been reported that the bottom surface of the films conforms to the surface of the petri dishes. The surface roughness of the petri dishes used also in this study has been quantified to be approximately 0.25 μm , corresponding approximately to the roughness of the bottom surface of sample T100.
In Figure 7a, where the surface roughnesses are plotted as a function of mass fraction of TEMPO pretreated NFC, the top and bottom surface roughnesses decrease when the mass fraction of TEMPO NFC increases. As described by  the NFC made of P. radiata pulp fibres and pretreated with TEMPO is highly fibrillated, containing mostly structures with diameter less than 20nm. The NFC manufactured without pre-treatment has a broader dimensional distribution, containing also fibres and fibre fragments (Figure 8; ). Hence, the characterization performed in this study confirms that the top surface roughness represents unevenness caused by residual fibres. Additionally, the effect of well-fibrillated TEMPO NFC on the micro-porosity of the corresponding films is demonstrated in Figure 7b. Higher fraction of TEMPO NFC leads to lower micro-porosity.
Although the quantified porosity seems to be rather low, it is important to note that the pores in the NFC films assessed in this study occur in a wide range of size scales, as indicated, e.g., by Figures 2 and 8. Figure 9 shows the part of the pore volume distribution within the micro-porosity range detectable using X–μCT. The increased scatter towards larger pore volume is related to the relatively low statistics and the selected bin size (≈ 2 μm3). On the other hand, the films contain also pores in smaller size scales, created by the random deposition of the nanofibrils (Figure 8). Considering the quantified intrinsic thickness (Figure 3), the density of the films is roughly between 1100 and 1400 kg/m3, which is in accordance with densities reported previously . If it is assumed that the bulk density of NFC material is (1590±50) kg/m3 [35,36], a simple calculation shows that the total porosity is (21±4)% for all films in the present study. This suggests that only a small fraction of pores are in the micro-porosity range.
Based on the micro-porosity map in Figure 5, most of the micro-pores seem to be found at locations along residual fibres. This observation is confirmed for film T0 (Figure 10). By comparing the uniformly weighted thickness distribution to the thickness distribution weighted by local pore height, it is demonstrated that more pores are located at the relatively thick parts of the film. Such thick areas have been previously attributed to locations containing residual fibres (Figure 5). Similar reasoning applies to the other samples assessed in this study. Similarly to the roughness, the micro-porosity decreases when the mass fraction of TEMPO pretreated NFC increases (Figure 7b). Based on the presented results, it can thus be concluded that also the micro-porosity, in addition to roughness, is mainly caused by residual fibres.
2.2. Oxygen Transmission Rate
NFC films have been reported to be most adequate as barriers against oxygen [13,19,21,37], and thus the material has potential for food packaging applications. The OTR of sample T30 is approximately 3.7mLm−2 day−1 (measured at 60% RH, corresponding to oxygen permeability of 0.6mLμmm−2 day−1 kPa−1), which agrees with the OTR measured in  for 20 g/m2 films. There values of 4.12 and 3.68mLm−2 day−1 were determined for films similar to T0 and T100, respectively, measured at 50% RH. The relatively low OTR has been attributed to the high crystallinity of nanofibrils and the high fibrillation of the material, which facilitates the formation of dense film structures. However, cellulose is hygroscopic and the OTR of neat NFC films increases with increasing relative humidity [21,38,39]. This phenomenon is observed also in the films used in this work. At high relative humidity, water limits the hydrogen bonding between adjacent nanofibrils inducing an opening of the dense structures and thus reducing the packing of the fibrillated material . Considering sample T30, this study exemplifies that there is a considerable increase in the OTR when the relative humidity increases to 80% (Figure 11a). It is important to emphasize that the OTR levels of the NFC films assessed in this study are comparable to ethylene vinyl alcohol (EVOH) (0.1–0.6mLμmm−2 day−1 kPa−1, 50% RH, 23 °C, ) and cellophane (3mLμmm−2 day−1 kPa−1, 50% RH, ). For a more detailed description of the barrier properties of various fibrillated materials see .
As shown in Figure 11b the film thickness increases significantly with increased humidity, confirming the swelling of the film. No hysteresis exceeding the scatter of the results near 60% RH is observable. Furthermore, no significant surface roughness or micro-porosity changes were quantified as a function of relative humidity.
2.3. Final Remarks
It is worth to emphasize that one of the advantages of using nanofibrillated cellulose is its renewability and biodegradability. Hence, NFC is a good alternative to, e.g., aluminium foil or petroleum based polymers, especially when it comes to barriers for food packaging. However, cellulose is hygroscopic and thus the films are affected by humidity. It is thus important to understand how the structure and barrier properties are affected by increased humidity, as we have demonstrated in this study. Moreover, due to the hygroscopic characteristics of NFC materials it is expected that the application of NFC in food packaging would require, e.g., addition of alternative components for reducing water intake and transmission. Some advances have been reported in this respect, considering also the grease resistance of the material (see  and references therein).
3. Experimental Section
3.1. Nanofibrillated Cellulose Films
Never dried Pinus radiata bleached market kraft pulp fibres were used in this study. The pulp fibres were homogenized with a Rannie 15 type 12.56X homogenizer, operated at 1000 bar pressure. The consistency of the pulp during homogenization was 0.5%. In addition, the bleached pulp fibres were pre-treated with TEMPO-mediated oxidation according to , and homogenized with the same conditions as above. The fibrillated materials were collected after 3 passes through the homogenizer. Five series of films of grammage 20 g/m2 were made by solution casting in petri dishes. The solid content of the NFC suspension was 0.2%. The series contained an increasing mass fraction of TEMPO pre-treated NFC, as described in Table 1.
A detailed quantification of the structural and chemical properties of the materials before and after homogenization has been done previously in  and , and is not repeated here. In the previous work it was noted that NFC manufactured without TEMPO pre-treatment is heterogeneous and contains a considerable amount of non-fibrillated fibres that are mostly absent in the TEMPO pre-treated NFC. The diameters of the fibrils in the TEMPO pre-treated material are thus mostly less than 20nm, whereas in the non-pre-treated case the diameter distribution is broader, extending to approximately 60nm (not counting the non-fibrillated fibres, ).
3.2. X-ray Microtomography
For X–μCT analysis, approximately 1mm × 4mm samples were cut and glued on top of a sample holder rod. X-ray microtomographic images of the samples were acquired using XRadia μCT-400 device (XRadia, Concord, CA, USA) with voxel size of 0.58 μm, resulting in imaged film volume of approximately 1mm2 × film thickness. The relative humidity and temperature during the X–μCT scans were approximately 30% and 23 °C, respectively. As the contrast-to-noise ratio between film and background was high (>10), the images were binarized using thresholding (see also Figure 2). The threshold value was decided using the Otsu method  and it was kept constant for all the images. After thresholding the bulk of the film was of value one whereas the background and the pores were zeroed. As voxels belonging to the film were mostly connected to each other, any artifacts were removed by zeroing all regions whose volume was less than 1000 voxels. Being located outside of the bulk of the film, the removal of the artifacts did not affect the detected porosity.
The surface topography maps were extracted for both surfaces, based on the borders between the binarized film and air. The acquired maps were processed with the ImageJ software using the SurfCharJ plugin . The roughness described by the root-mean-square surface height Sq was quantified at wavelengths less than 160 μm.
To facilitate the determination of pore size distribution, the binary image was inverted and voxels above the top surface and below the bottom surface were zeroed, leaving only the pores visible. The volume of each pore was calculated and the results were binned to yield the pore size distribution. A porosity map was also determined by considering the local height of pores corresponding to each pixel at the surface maps.
The thickness map of the film was determined as the local distance between the top and the bottom surfaces. The values of the thickness map were binned with uniform weight to yield the thickness distribution of film area. The binning was repeated using local pore height as weight to visualize the correlation between the local amount of pores and the thickness. Correlation coefficients between surface maps and thickness maps were determined using the CorrelationJ plugin . From each material, at least 3 replicates were processed as indicated in Table 1.
To quantify the film structure in varying relative humidity, a special chamber was constructed, see Figure 12. The chamber was made of 0.1mm thick Polyether ether ketone (PEEK). PEEK was chosen as wall material as it is resistant to X-ray damage and has favourable machining properties. The chamber, containing the sample, was placed in the X–μCT device and air with predetermined relative humidity was constantly pumped through it using a HumiSys HF humidity generator (InstruQuest, Boca Raton, FL, USA). As the humidity generator and parts of required piping were located outside of a radiation protection cabinet, possibly in a different temperature from the sample, the relative humidity in the chamber was measured using a Sensirion SHT21 miniature sensor (Sensirion, Staefa, Switzerland). Before starting the X–μCT scan, the sample was let to stabilize for 4 hours. After the scan was finished, the relative humidity of the incoming air was adjusted to the desired level and the stabilization and the X–μCT scanning procedure was repeated. In the process the relative humidity was first cycled from 20% to 60%, where the scanning was paused for some days and the sample was returned to room humidity, approximately 30%. To reveal possible hysteresis in the structure and to quantify the precision of the measurement, the cycling was repeated from 60% RH to 80% RH and back to 60% RH.
X–μCT imaging process is very sensitive to instability and movement of the sample. As the X–μCT images didn’t contain any typical artifacts resulting from movement of the sample, we concluded that the four hour stabilization period was long enough. Being a time-consuming process, the sequence was performed for a single material only. Film T30 was chosen as it was expected to have high porosity but still being affected by the addition of TEMPO NFC. The resulting X–μCT images were processed similarly to those from non-humidity controlled scans.
3.3. Electron Microscopy
To visualize the surface of the films, pieces of samples T0 and T100 were assessed with scanning electron microscopy. Low magnification images (500×) were acquired with a Hitachi S-3000 variable pressure SEM (Hitachi High-Technologies Corporation, Minatoku, Tokyo, Japan), in secondary electron imaging mode. High-magnification images (50; 000×) were acquired from areas without gold coating, with a Zeiss Ultra field-emission SEM, using an inlens detector. The working distance and acceleration voltage were <1 mm and 0.5 kV, respectively. For details see .
For SEM cross-sectional analysis, pieces of 10mm × 20mm from each film were dried at 105 °C for 1 h and embedded in epoxy resin. The embedded samples were hand-held ground, and polished with polishing clothes of 9 and 1 μm. The prepared blocks were coated with a layer of carbon for SEM analysis. The microscope was a Hitachi S-3000 variable pressure SEM. Ten SEM cross-sectional images were acquired randomly from each film sample, applying the backscatter electron imaging (BEI) mode. The magnification was 500×, giving a resolution of 0.1 μm. The images were thresholded automatically according to Otsu . The cross-sectional thickness was automatically quantified considering the upper and lower borders between the films and the epoxy resin.
3.4. Laser Profilometry
For laser profilometry (LP) analysis, samples of 10mm × 10mm were placed on an object glass with double-sided tape and coated with a layer of gold. Ten laser profilometry (Lehmann, Lehman Mess-Systeme AG, Baden-Dättwil, Germany) topography images were acquired from each sample. The size of the local areas was 1mm × 1mm, having a resolution of 1 μm/pixel. The LP image acquisition was performed at 50% RH and 23 °C. The acquired images were processed similarly to the surface topography maps extracted from the X–μCT images. The LP analysis was conducted on the top and on the bottom sides of the films.
3.5. Apparent Thickness
The apparent thickness of each film was measured using L & W Micrometer 51 from ten local areas, and the results were averaged to yield the apparent thickness for each film type. The thickness measurements were performed according to ISO 534 standard.
3.6. Oxygen Transmission Rate
The oxygen transmission rate (OTR) of sample T30 was measured with a Mocon OX-TRAN® 1/50 at 20%, 40%, 60% and 80% relative humidity. The OTR of NFC films within the same series and measured at the same RH is relatively stable [22,34]. We have therefore undertaken only one OTR measurement for each humidity level.
X-ray computed tomography gives estimates comparable with LP and SEM for roughness and thickness of NFC films, respectively. An advantage of X-ray computed tomography is spatially isotropic resolution that allows analysis of micro-porosity and three-dimensional structural features. Based on a recently developed in-situ humidity chamber, the method allows also a robust control over environmental conditions during imaging, thereby enabling structural analyses of the same sample in different humidity conditions.
Additionally, the results of this study suggest that the fraction of residual fibres influences the micro-roughness and micro-porosity of NFC films. The large fraction of residual fibres encountered in sample T0 contributes to the formation of rough film structures, increasing the surface roughness and the micro-porosity. On the other hand, in sample T100 the residual fibres are absent, leading to smooth and dense structures.
This project has been partially funded through European Union Regional Development Fund FuFiPro project. Part of this work was supported by the Research Council of Norway, through the NanoHeal project, grant no. 219733. The authors acknowledge Riikka Hirvelä and Solja Ala-Korpi for valuable laboratory work during the experiments.
Conflicts of Interest
The authors declare no conflicts of interest.
- Author ContributionsGary Chinga-Carrasco has taken care of manufacturing the materials and performing the scannig electron microscopy, laser profilometry and oxygen transmission rate measurements. Arttu Miettinen and Markku Kataja have performed the X-ray microtomographic measurements, including development of the humidity-controlled microtomographic scanning system. All the authors have taken part in the interpretation of the results.
- Heyn, A. The elementary fibril and supermolecular structure of cellulose in soft wood fiber. J. Ultrastruct. Res 1969, 26, 52–68. [Google Scholar]
- Frey-Wyssling, A. The fine structure of cellulose microfibrils. Science 1954, 119, 80–82. [Google Scholar]
- Somerville, C. Cellulose synthesis in higher plants. Annu. Rev. Cell Dev. Biol 2006, 22, 53–78. [Google Scholar]
- Mutwil, M.; Debolt, S.; Persson, S. Cellulose synthesis: A complex complex. Curr. Opin. Plant Biol 2008, 11, 252–257. [Google Scholar]
- Chinga-Carrasco, G. Cellulose fibres, nanofibrils and microfibrils: The morphological sequence of MFC components from a plant physiology and fibre technology point of view. Nanoscale Res. Lett 2011, 6, 417. [Google Scholar]
- Turbak, A.; Snyder, F.; Sandberg, K. Microfibrillated cellulose, a new cellulose product: Properties, uses, and commercial potential. J. Appl. Polym. Sci. Appl. Polym. Symp 1983, 37, 815–827. [Google Scholar]
- Saito, T.; Nishiyama, Y.; Putaux, J.L.; Vignon, M.; Isogai, A. Homogeneous suspensions of individualized microfibrils from TEMPO-catalyzed oxidation of native cellulose. Biomacromolecules 2006, 7, 1687–1691. [Google Scholar]
- Wågberg, L.; Decher, G.; Norgren, M.; Lindström, T.; Ankerfors, M.; Axnäs, K. The build-up of polyelectrolyte multilayers of microfibrillated cellulose and cationic polyelectrolytes. Langmuir 2008, 24, 784–795. [Google Scholar]
- Syverud, K.; Chinga-Carrasco, G.; Toledo, J.; Toledo, P. A comparative study of Eucalyptus and Pinus radiata pulp fibres as raw materials for production of cellulose nanofibrils. Carbohydr. Polym 2010, 84, 1033–1038. [Google Scholar]
- Alila, S.; Besbes, I.; Red Vilar, M.; Mutjé, P.; Boufi, S. Non-woody plants as raw materials for production of microfibrillated cellulose (MFC): A comparative study. Ind. Crops Prod 2013, 41, 250–259. [Google Scholar]
- Taniguchi, T.; Okamura, K. New films produced from microfibrillated natural fibres. Polym. Int 1998, 47, 291–294. [Google Scholar]
- Henriksson, M.; Berglund, L. Structure and properties of cellulose nanocomposite films containing melamine formaldehyde. J. Appl. Polym. Sci 2007, 106, 2817–2824. [Google Scholar]
- Syverud, K.; Stenius, P. Strength and permeability of MFC films. Cellulose 2009, 16, 75–85. [Google Scholar]
- Mörseburg, K.; Chinga-Carrasco, G. Assessing the combined benefits of clay and nanofibrillated cellulose in layered TMP-based sheets. Cellulose 2009, 16, 795–806. [Google Scholar]
- Chinga-Carrasco, G.; Tobjörk, D.; Österbacka, R. Inkjet-printed silver-nanoparticles on nano-engineered cellulose films for electrically conducting structures and organic transistors—Concept and challenges. J. Nanopart. Res 2012, 14, 1213. [Google Scholar]
- Orelma, H.; Filpponen, I.; Johansson, L.S.; Österberg, M.; Rojas, O.; Laine, J. Surface functionalized nanofibrillar cellulose (NFC) film as a platform for immunoassays and diagnostics. Biointerphases 2012, 7, 1–12. [Google Scholar]
- Henriksson, M.; Berglund, L.; Isaksson, P.; Lindström, T.; Nishino, T. Cellulose nanopaper structures of high toughness. Biomacromolecules 2008, 9, 1579–1585. [Google Scholar]
- Lavoine, N.; Desloges, I.; Dufresne, A.; Bras, J. Microfibrillated cellulose—Its barrier properties and applications in cellulosic materias: A review. Carbohydr. Polym 2012, 90, 735–764. [Google Scholar]
- Fukuzumi, H.; Saito, T.; Iwata, T.; Kumamoto, Y.; Isogai, A. Transparent and high gas barrier films of cellulose nanofibers prepared by TEMPO-mediated oxidation. Biomacromolecules 2009, 10, 162–165. [Google Scholar]
- Rodionova, G.; Lenes, M.; Eriksen, O.; Gregersen, O. Surface chemical modification of microfibrillated cellulose: Improvement of barrier properties for packaging applications. Cellulose 2011, 18, 127–134. [Google Scholar]
- Aulin, C.; Gällstedt, M.; Lindström, T. Oxygen and oil barrier properties of microfibrillated cellulose films and coatings. Cellulose 2010, 17, 559–574. [Google Scholar]
- Chinga-Carrasco, G.; Syverud, K. On the structure and oxygen transmission rate of biodegradable cellulose nanobarriers. Nanoscale Res. Lett 2012, 7, 192. [Google Scholar]
- Chinga-Carrasco, G.; Averianova, N.; Kodalenko, O.; Garaeva, M.; Petrov, V.; Leinsvang, B.; Karlsen, T. The effect of residual fibres on the micro-topography of cellulose nanopaper. Micron 2014, 56, 80–84. [Google Scholar]
- Andresen, M.; Johansson, L.S.; Tanem, B.; Stenius, P. Properties and characterization of hydrophobized microfibrillated cellulose. Cellulose 2006, 13, 665–677. [Google Scholar]
- Pääkkö, M.; Ankefors, M.; Kosonen, H.; Nykänen, A.; Ahola, S.; Österberg, M.; Ruokolainen, J.; Laine, J.; Larsson, P.; Ikkala, O.; et al. Enzymatic hydrolysis combined with mechanical shearing and high-pressure homogenization for nanoscale cellulose fibrils and strong gels. Biomacromolecules 2007, 8, 1934–1941. [Google Scholar]
- Abe, K.; Iwamoto, S.; Yano, H. Obtaining cellulose nanofibers with a uniform width of 15nm from wood. Biomacromolecules 2007, 8, 3276–3278. [Google Scholar]
- Ahola, S.; Österberg, M.; Laine, J. Cellulose nanofibrils—Adsorption with poly(amideamine) epichlorohydrin studied by QCM-D and application as a paper strength additive. Cellulose 2008, 15, 303–314. [Google Scholar]
- Syverud, K.; Xhanari, K.; Chinga-Carrasco, G.; Yu, Y.; Stenius, P. Films made of cellulose nanofibrils—Surface modification by adsorption of a cationic surfactant and characterisation by computer-assisted electron microscopy. J. Nanopart. Res 2010, 13, 773–782. [Google Scholar]
- Chinga-Carrasco, G.; Yu, Y.; Diserud, O. Quantitative electron microscopy of cellulose nanofibril structures from Eucalyptus and Pinus radiata kraft pulp fibres. Microsc. Microanal 2011, 17, 563–571. [Google Scholar]
- Kak, A.; Slaney, M. Principles of Computerized Tomographic Imaging; IEEE Press: New York, NY, USA, 1988. [Google Scholar]
- Otsu, N. A threshold selection method from gray level histograms. IEEE Trans. Syst. Man Cybern 1979, 9, 62–66. [Google Scholar]
- Chinga, G.; Johnssen, P.; Dougherty, R.; Lunden-Berli, E.; Walter, J. Quantification of the 3-D micro-structure of SC surfaces. J. Microsc 2007, 227, 254–265. [Google Scholar]
- Chinga, G.; Syverud, K. Quantification of paper mass distributions within local picking areas. Nordic Pulp Paper Res. J 2007, 22, 441–446. [Google Scholar]
- Chinga-Carrasco, G.; Kuznetsova, N.; Garaeva, M.; Galiullina, G.; Kostochko, A.; Leirset, I.; Syverud, K. Bleached and unbleached MFC nanobarriers - properties and hydrophobization with hexamethyldisilazane. J. Nanopart. Res 2012, 14, 1280. [Google Scholar]
- Stone, J.; Scallan, A.; Aberson, G. The wall density of native cellulose fibres. Pulp Paper Mag. Can 1966, 67, 263–268. [Google Scholar]
- Diddens, I.; Murphy, B.; Krisch, M.; Müller, M. Anisotropic elastic properties of cellulose measured using inelastic X-ray scattering. Macromolecules 2008, 41, 9755–9759. [Google Scholar]
- Siro, I.; Plackett, D.; Hedenqvist, M.; Ankerfors, M.; Lindström, T. Highly transparent films from carboxymethylated microfibrillated cellulose: The effect of multiple homogenization steps on key properties. J. Appl. Polym. Sci 2011, 119, 2652–2660. [Google Scholar]
- Yang, Q.; Fukuzumi, H.; Saito, T.; Isogai, A.; Zhang, L. Transparent cellulose films with high gas barrier properties fabricated from aqueous alkali/urea solutions. Biomacromolecules 2011, 12, 2766–2771. [Google Scholar]
- Waggoner, R.; Blum, F.; MacElroy, J.M.D. Dependence of the solvent diffusion coefficient on concentration in polymer solutions. Macromolecules 1993, 26, 6841–6848. [Google Scholar]
- Byun, Y.J.; Hong, S.; Kim, K.; Jeon, D.; Kim, J.; Whiteside, W.; Park, H.J. Physical and chemical properties of -irradiated EVOH film. Radiat. Phys. Chem 2007, 76, 974–981. [Google Scholar]
|Series||NFC (%)||TEMPO NFC (%)||Number of replicates in X–μCT|
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