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. 2011 Jul 15;18(5):1227–1237. doi: 10.1007/s10570-011-9576-1

Cellulose nanofibrils as filler for adhesives: effect on specific fracture energy of solid wood-adhesive bonds

Stefan Veigel 1,✉, Ulrich Müller 2, Jozef Keckes 3, Michael Obersriebnig 1, Wolfgang Gindl-Altmutter 1
PMCID: PMC4579863  PMID: 26412949

Abstract

Cellulose nanofibrils were prepared by mechanical fibrillation of never-dried beech pulp and bacterial cellulose. To facilitate the separation of individual fibrils, one part of the wood pulp was surface-carboxylated by a catalytic oxidation using (2,2,6,6-tetramethylpiperidin-1-yl)oxyl (TEMPO) as a catalyst. After fibrillation by a high pressure homogenizer, the obtained aqueous fibril dispersions were directly mixed with different urea–formaldehyde-(UF)-adhesives. To investigate the effect of added cellulose filler on the fracture mechanical properties of wood adhesive bonds, double cantilever beam specimens were prepared from spruce wood. While the highest fracture energy values were observed for UF-bonds filled with untreated nanofibrils prepared from wood pulp, bonds filled with TEMPO-oxidized fibrils showed less satisfying performance. It is proposed that UF-adhesive bonds can be significantly toughened by the addition of only small amounts of cellulose nanofibrils. Thereby, the optimum filler content is largely depending on the adhesive and type of cellulose filler used.

Keywords: Cellulose, Nanofibrils, Filler, Adhesive, Fracture energy

Introduction

Bonding of solid wood is a key issue in the manufacturing of numerous wood products. Especially regarding applications in the structural field, mechanical performance of wood-adhesive bonds is of fundamental importance. Apart from other influencing factors like adherend material, geometric design of the bond line and its loading conditions, the adhesive properties significantly impact the strength of an adhesive bond (Habenicht 2002). In this regard, the addition of fibrous fillers to the liquid adhesive is one potential opportunity of increasing strength. Organic flours that are commonly applied as fillers for urea–formaldehyde-(UF)-adhesives primarily improve the processing characteristics of the adhesive mixture, although they may contribute to bonding strength by agglutination of starch during hot pressing (Dunky and Niemz 2002). If fibers are added to the adhesive, the cured adhesive bond line may be considered as a fiber-reinforced polymer. From composite science it is known, that the smaller the fiber diameter, the higher the attainable strength will be (Griffith 1920). Consequently, there were several attempts in the past to improve the mechanical performance of adhesive joints by reinforcing the adhesive with nanoparticles (Zhang et al. 2008; Ahmad et al. 2010; May et al. 2010; Khoee and Hassani 2010) or nanofibers (Hsiao et al. 2003; Ureña et al. 2008; Khalili et al. 2008, 2009; Prolongo et al. 2009, 2010; Yoon et al. 2010) from high-strength materials.

Unlike in the past, where predominantly glass fibers, polymeric fibers and carbon fibers were used for adhesive reinforcement, nanofibrils from cellulose were used in this study. This abundant biopolymer offers outstanding mechanical properties especially when it is applied as a nano-scale material. The crystalline part of the cellulose has an estimated strength of up to 10 GPa (Zimmermann et al. 2004) and an elastic modulus in the range of 138 GPa (Sakurada et al. 1962; Nishino et al. 1995). Although the values determined for cellulose nanofibrils (CNF) are lower due to paracrystalline regions and material degradation during processing, fibrils based on cellulose can be considered as fairly competitive to synthetic fiber materials. This is especially true when the low density of cellulose is taken into consideration.

Two recently published articles address for the first time the application of CNF for wood-adhesive reinforcement. In a study performed by López-Suevos et al. (2010), the suitability of CNF for the preparation of polyvinylacetate-(PVAc)-bond lines with improved temperature resistance was investigated. For this purpose, lap shear specimens according to EN 205 with a cellulose content of up to 3 wt% were prepared and tested to failure. Although the cellulose-reinforced bond lines generally performed worse in dry and wet conditions, the bonds showed superior heat resistance.

Richter et al. (2009) tried to improve the rheological behavior and bonding properties of two different wood-adhesives (i.e. one component polyurethane-(1C-PUR)-adhesive and water-based polyvinyl acetate latex-(PVAc)-adhesive) by adding CNF. Among other things, lap-shear testing according to EN 302-1 as well as block shear testing was performed. Cellulose content of the adhesive mixtures was increased up to 10 wt% for 1C-PUR and 1.33 wt% for the PVAc-adhesive. PVAc-adhesive films with cellulose reinforcement showed a direct correlation between the CNF-content of the adhesive formulation and the stiffness and strength properties of corresponding films. In spite of this, no significant and consistent improvement of bond line performance compared to non-reinforced reference products was achieved neither for PUR nor for PVAc. According to Richter et al. (2009), a quality controlled fibril morphology, a homogeneous dispersion into the adhesive as well as a comparable polarity of fibrils and adhesive polymers are critical parameters affecting the mechanical performance of the adhesive bond.

In contrast to the studies mentioned above, two different UF-adhesives were used in the present study. These resins generally show a much more brittle material behavior than PVAc- and 1C-PUR-adhesives. Therefore, UF-adhesives tend to create micro-cracks that limit the mechanical performance of UF-bonds. Own investigations revealed that longitudinal shear strength of UF-bonds can be improved up to 30% by adding about 5 wt% of CNF to the liquid adhesive (Eichhorn et al. 2009). Since apart from strength, also strain to failure was found to be considerably higher, it was concluded that the UF-adhesive was possibly toughened by the addition of CNF. Consequently it is the aim of the present study to evaluate a potential effect of a CNF-addition on the specific fracture energy of UF-adhesive bonds.

Materials and methods

Preparation and characterization of CNF

For the preparation of CNF-dispersions, never dried dissolving grade beech pulp (Lenzing AG, Lenzing, Austria) with an initial solid content of about 50% was used as a starting material. One half of the pulp was directly used for high pressure homogenization, i.e. without further pretreatment (P1), while the other half was chemically modified by carboxylation (P2) with the aim of facilitating the separation of individual cellulose fibrils during the following homogenization process. The P2-dispersion was prepared by direct surface carboxylation using (2,2,6,6-tetramethylpiperidin-1-yl)oxyl (TEMPO) as a catalyst and sodium chlorite as a primary oxidant under neutral conditions as described by Saito et al. (2009). Apart from wood pulp, also bacterial cellulose (BC) was used for CNF preparation. The celluloses (P1, P2 and BC) were suspended in distilled water and fibrillated by 20 passes through a high pressure laboratory homogenizer (APV 1000, APV Manufacturing Sp. z o.o., Bydgoszcz, Poland) with a pressure of up to 850 bar. After homogenization, the dispersions were air dried at 60 °C to increase the cellulose content to about 4% by weight.

To evaluate the degree of fibrillation, dried cellulose fibrils were sputter-coated with 7.5 nm of platinum and observed by a field emission scanning electron microscope (FE-SEM, Nova NanoSEM 230, Hillsboro, USA). In order to verify potential effects of TEMPO modification on the structure of cellulose fibrils, wide-angle X-ray diffraction (WAXD) was performed with dried cellulose films using a Nanostar (Bruker AXS) system connected to a rotating anode generator with Cu target. The system is equipped with crossed Göbel mirrors, a pinhole system for a primary collimation with a beam diameter of 100 μm and a two dimensional (2D) wire detector (Hi-Star). The 2D detector images were acquired and evaluated using Fit2D software.

To investigate a potential effect of cellulose addition on the adhesive’s cure rate, the pH value and buffer capacity of the cellulose dispersions were determined using a microprocessor-pH-meter (CG 840, Schott Geräte GmbH, Hofheim a. Ts., Germany) equipped with a pH/temperature combination electrode (N 1042 A). The buffer capacity was determined by titrating 10 mL of the cellulose dispersion (cellulose content 1% by weight) with 0.1 M sulphuric acid until a pH value of 2 was reached. Average buffer capacity values were calculated for the pH range from 2 to 7 by dividing the amount of acid consumed by the resulting change in pH.

Preparation of double cantilever beam-(DCB)-specimens

For fracture energy testing, the simplified flat double cantilever beam-(DCB)-specimen geometry as described by Gagliano and Frazier (2001) was applied. The specimen consists of two wood adherends with a 3° longitudinal grain angle. Since the grain of both adherends converges to a V-shape at the bond line (Fig. 1), wood failure can be reduced to a minimum. Flawless spruce wood (Picea abies Karst.) with a density of 450 ± 18 kg/m³ was bonded with two UF-adhesives, namely a non-structural powder-adhesive for solid wood bonding (UF-1, W-Leim Spezial, Dynea Austria GmbH, Krems, Austria) and a low viscosity UF-adhesive used in particle board production (UF-2, Prefere 10F101, Dynea Austria GmbH, Krems, Austria). According to the manufacturer’s instructions, UF-1 was mixed with water in a weight ratio of 5:3. For the preparation of cellulose-filled adhesives, the powder was mixed with the fibrillated cellulose dispersions instead of water. To achieve proper dispersion of cellulose fibrils within the adhesive, mixing was performed with a hand blender for 3 min. It is worth mentioning that in case of P2, small cellulose particles could be visually observed even after mixing with the adhesive. Adhesive mixtures with a cellulose content of 0.5, 1.0, 1.5 and 2.0% per unit weight of cured UF were prepared with both adhesives. A spreading quantity of 250 g/m² of solid resin was used for all adhesive assemblies. The specimens bonded with UF-1 were cured at room temperature using a pressure of 0.8 MPa. As usual in the production of particle boards, ammonium sulphate (3% by unit weight of cured UF) was used as a hardener for UF-2. To avoid a further decrease in solid content, the powdery hardener was dissolved in the respective cellulose dispersion which was thereafter added to the adhesive. The composition of the individual adhesive mixtures and the resulting solid contents are summarized in Table 1. In the case of UF-2, apart from cellulose, a large amount of water is added to the adhesive system. Since it was assumed that this results in a decelerated adhesive cure, the gel times of all UF-2 adhesive mixtures were determined. Therefore, about 2 mL of the liquid adhesive were poured into a test tube and immersed in a boiling water bath. The time span from immersion until complete gelation of the adhesive represents the gel time. Adhesive joints prepared with UF-2 were cured at a temperature of 160 °C with a pressure of 0.5 MPa. Pressing time was 480 min for UF-1 and 15 min for UF-2. Under these conditions, complete curing can be assumed for both adhesive systems. The cured adhesive assemblies were cut to a final size of 200 × 20 × 20 mm³. For crack initiation, a 30 mm long ogival shaped kerf was cut at one end of each specimen. Two holes were drilled to attach the test grips. All specimens were stored at 20 °C and 65% relative humidity until equilibrium moisture content was reached.

Fig. 1.

Fig. 1

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Geometry of flat double cantilever beam-(DCB)-specimens used for fracture energy determination of wood adhesive joints. All dimensions in mm

Table 1.

Composition and gel times of adhesive mixtures

Adhesive mixture Cellulose content (wt% of cured UF) Quantity (g/100 g adhesive mixture) Total solid content (%) Gel time (s)
Cellulose Water Hardener
UF-1 0 0.00 37.50 – 62.5 –
UF-1+P1/P2/BC 0.5 0.31 37.19 – 62.8 –
1.0 0.63 36.88 63.1
1.5 0.94 36.56 63.4
2.0 1.25 36.25 63.8
UF-2 0 0.00 33.34 1.94 66.7 55
UF-2+P1 0.5 0.30 38.16 1.79 61.8 59
1.0 0.56 42.28 1.66 57.7 65
1.5 0.78 45.86 1.55 54.1 70
2.0 0.97 49.00 1.46 51.0 73
UF-2+P2 0.5 0.30 38.16 1.79 61.8 57
1.0 0.55 42.29 1.66 57.7 60
1.5 0.78 45.87 1.55 54.1 65
2.0 0.97 49.00 1.46 51.0 68
UF-2+BC 0.5 0.30 38.48 1.78 61.5 60
1.0 0.55 42.84 1.65 57.2 67
1.5 0.77 46.60 1.53 53.4 73
2.0 0.96 49.86 1.43 50.1 78
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UF-1, UF-2 pure adhesives, Cellulose nanofibrils prepared from P1 untreated pulp, P2 TEMPO-oxidized pulp and BC bacterial cellulose

Mechanical testing

Fracture testing was performed on a Zwick/Roell Z100 universal testing machine equipped with a 2.5 kN load cell. The DCB-specimens were initially loaded with a speed of 1 mm/min. After a 50% drop in load, testing speed was increased steadily to a value of 10 mm/min. The specimens were tested until complete separation of the two parts and the load–displacement curve was recorded. Specific fracture energy (J/m²) was calculated by relating the total fracture energy obtained by integration of the load–displacement curve to the bonding surface area. All specimens with a wood failure greater than 10% were dropped out of the analysis. For the individual groups of specimens, mean values were calculated and compared by one-way analysis of variance (ANOVA, p ≤ 0.05).

Characterization of cured bond lines

The cured bond lines were characterized using nanoindentation and optical microscopy. Small cubes with dimensions of 2 × 2 × 1 mm³ (width × thickness × length) containing the bond line in the center, were cut out of the DCB-specimens that had not been tested. The cubes were infiltrated with embedding medium (Agar Low Viscosity Resin R1078, Agar Scientific Ltd, Stansted, England) which was cured in an oven at 60 °C for 24 h. The cured resin blocks were cut to a size of 2 × 2 × 2 mm³ (width × thickness × length) and a smooth surface was prepared by an ultramicrotome (Leica Ultracut R, Leica Microsystems, Wetzlar, Germany). The specimens were used for incident light microscopy (Axioplan 2 imaging, Carl Zeiss Microimaging GmbH, Jena, Germany) and subsequently for nanoindentation.

The nanoindentation measurements were performed on a Hysitron TI-900 TriboIndenter equipped with a Berkovich tip. Four specimens were tested for each adhesive type (two specimens with pure adhesive bond lines and two bond lines filled with 2 wt% of P1). Indentation was performed in load-controlled mode using a pre-force of 2 μN. A 3-phase load profile was applied consisting of a loading phase where a load of 500 μN was applied within 1 s, a constant load phase with a duration of 20 s and an unloading phase lasting 1 s. For each indent, a load-depth curve was recorded and used to calculate the total work of indentation (Wtot) which can be further divided into an elastic (We) and plastic (Wp) part. The ratio of We/Wp may be used to estimate the brittleness of the adhesive bond line. Indentation hardness was calculated by dividing the peak load by the contact area at the end of the constant load phase. As described by Konnerth et al. (2006), the reduced elastic modulus (Er) was calculated from the initial slope of the unloading curve and indentation creep (CIT) was defined as the relative change of the indentation depth while the applied load is held constant.

Results and discussion

Characterization of cellulose nanofibrils

After high-pressure homogenization, differences in the optical appearance of cellulose fibril suspensions were observed. Unlike the unmodified P1- and BC-dispersions, which were opaque, the TEMPO-treated P2-dispersion was optically transparent and showed a considerably higher viscosity at equal cellulose content. Since the viscosity further increased when water was removed from the suspension by drying, the P2-dispersion behaved almost like a solid when dried to a cellulose content of 4%. At this content, the P2-dispersion took up the form of a gelatinous granulate with particles of different size, whereas the P1 and BC suspensions, respectively, were still liquid, though highly viscous.

FE-SEM microscopy confirmed differences in the structure of TEMPO-treated and untreated fibrils. As shown in Fig. 2, the untreated P1- and BC-nanofibrils form a loose fibril network after vacuum drying of the corresponding dispersions. In strong contrast, the TEMPO-treated P2-fibrils agglomerate to a very compact film when dried. This may be due to the fact that the introduction of carboxylate groups during the TEMPO-mediated oxidation causes significant changes in the surface properties of cellulose fibrils. Measurement of fibril diameters from the FE-SEM images revealed smaller fibrils for P2 compared to P1 and BC, respectively. The mean fibril diameters were 61 ± 21 nm (P2), 96 ± 48 nm (P1) and 109 ± 56 nm (BC) whereas 50–60 fibrils have been measured for each cellulose material. The fibril diameters obtained in this study seem rather high when compared to the results of previous studies (Saito et al. 2006, 2009; Iwamoto et al. 2010). This is probably because the fibril dispersions were used directly after homogenization without separating larger aggregates by centrifugation. Also, an additional sonication step might have further decreased the fibril size.

Fig. 2.

Fig. 2

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FE-SEM micrographs of cellulose nanofibrils prepared by high pressure homogenization of BC bacterial cellulose and P1 untreated beech pulp as well as P2 TEMPO-oxidized pulp

Since TEMPO-treatment seemed to have affected the fibril structure as indicated by FE-SEM images (Fig. 2), WAXD measurements were performed in order to reveal possible changes in their crystalline structure. Contrary to a previous study (Saito et al. 2009) where quite similar X-ray diffraction patterns were found for both untreated kraft pulp and TEMPO-oxidized pulp, the WAXD-images of native (P1) and TEMPO-treated (P2) cellulose obtained in the present study differ considerably (Fig. 3). All celluloses investigated showed peak scattering intensities typical of cellulose I (Borysiak and Garbarczyk 2003). While both, P1 and BC are highly crystalline, TEMPO-treatment seems to have significantly reduced the crystallinity of P2. This is particularly obvious when a simple crystallinity index c is calculated from the scattering intensity Ic of the cellulose 200 reflection at an angle of 22.7° and the intensity Iref measured at an angle of 33°, where hardly any crystalline scattering was observed (Eq. 1).

graphic file with name M1.gif 1

Fig. 3.

Fig. 3

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X-ray diffraction patterns of cellulose films prepared by air drying of cellulose fibril dispersions (P1 untreated pulp, P2 TEMPO-oxidized pulp, BC bacterial cellulose). Intensity peaks are less pronounced for P2, indicating that the TEMPO-mediated oxidation caused a reduction in the degree of cellulose crystallinity

The crystallinity index c is highest for BC with 0.98 and P1 with 0.94 and significantly reduced for P2 with 0.84. In addition, it seems that not only the overall crystallinity of the cellulose fibrils was affected by TEMPO-modification, but also the average crystallite width. An assessment of the width of the cellulose 200 reflection peak at half the maximum intensity (full width at half maximum) for P1 and P2 shows a significant peak broadening in P2-cellulose. Since according to the Scherrer formula (Scherrer 1918) the peak width is inversely proportional to the crystallite size, this indicates a reduction of the width of cellulose crystallites after TEMPO-treatment.

Regarding their acid/base properties the three cellulose dispersions did not differ significantly. The initial pH values determined for P1, P2 and BC were 7.11, 7.43 and 7.02, respectively. The average buffer capacities were found to be 4.93, 6.75 and 5.60 mmol/L for the pH range from 2 to 7. Since the drop in pH caused by the addition of the acidic hardener by far compensates such low buffer capacities, the effect on adhesive’s cure can be neglected. The increase of gel times with increasing cellulose content (Table 1) is therefore predominantly attributed to the lower solid contents of CNF-filled UF-2 adhesive mixtures.

Characterization of cured adhesive bond lines

An analysis using incident light microscopy (Fig. 4) revealed that for UF-1, bond line thickness clearly increased due to the addition of P1. This effect is primarily attributed to the high viscosity of the filled adhesive. Although the increase in viscosity was not quantified, the markedly higher viscosity of UF-1 + P1 and BC was clearly visually recognizable. In contrast, UF-1 + P2 showed almost the same viscosity and bond line thickness than pure UF-1. As mentioned earlier, visible particles of P2 remained after mixing. Due to the strong agglomeration tendency of P2 it was obviously not possible to achieve a uniform distribution of individual fibrils in the adhesive.

Fig. 4.

Fig. 4

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Optical micrographs of urea–formaldehyde-(UF) bond lines. Two different adhesives were applied, once without any additional filler (UF-1 and UF-2) and once filled with 2 wt% fibrillated pulp (P1). Adhesive spread was 250 g/m² of solid resin in all cases

In the case of UF-2, bond lines were generally thinner and bond line thickness did not increase substantially for the cellulose filled adhesives. The low thickness can be explained by the much lower viscosity of pure UF-2 compared to UF-1. While for UF-1 the total solid content remains roughly the same after cellulose addition, this is not true for UF-2. Since in case of the latter the solid content is reduced by the addition of extra water from the cellulose dispersion, viscosity increase is less pronounced than for UF-1. Therefore a considerable amount of both pure and cellulose filled UF-2 was squeezed out during pressing. As evident from Fig. 4, the P1-filler markedly reduced penetration of UF-2 into the cellular wood cavities. Although only slightly higher than for the pure adhesive, the increased viscosity of UF-2 + P1 might be responsible for that. It can be assumed that this is also true for UF-2 filled with P2 and BC since the bond line morphology was quite similar. Same as for UF-1, large particles of P2 remained within the adhesive after mixing by means of a hand held blender (Fig. 5).

Fig. 5.

Fig. 5

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Polarized light micrograph of liquid urea–formaldehyde-(UF-2)-adhesive filled with 2 wt% TEMPO-oxidized pulp (P2). Large particles of P2 remain after mixing with the adhesive. The small bright dots represent crystalline adhesive constituents

Potential effects of CNF on the mechanical properties of the cured adhesive itself were studied by means of nanoindentation. The results of these experiments are summarized in Table 2. First of all, the two UF-resins used in the present study showed significantly different mechanical properties as UF-1 was clearly harder and stiffer than UF-2. The addition of 2 wt% CNF resulted in a decrease in stiffness and hardness for UF-1, whereas a slight increase was observed for UF-2. However, these changes were not significant in a statistical sense (T test, p ≤ 0.05). In addition to hardness and stiffness, the total work of indentation, the ratio between the elastic and plastic component of the work of indentation, and a creep factor were evaluated (Table 2). Particularly the ratio between the elastic and plastic component of the work of indentation is a good measure for the ductility of the adhesive. UF-2 turns out to be clearly more ductile than UF-1 and just as with hardness and stiffness, the ductility of adhesives as inferred from nanoindentation is not significantly affected by the addition of CNF. Considering the small percentage of cellulose added and the comparably high stiffness of UF-systems, a significant change in nanoindentation properties due to CNF addition, as observed for comparably soft hydroxypropyl cellulose (Zimmermann et al. 2005), would have been surprising. Thus, at least these results confirm that adhesive cure was apparently not affected in a negative manner by the addition of CNF, which is an important prerequisite for the further evaluation of macroscopic fracture experiments performed in the present study.

Table 2.

Results of nanoindentation measurements performed on cured urea–formaldehyde-(UF) bond lines

Adhesive Number of indents [1] Reduced modulus E r [GPa] Hardness H [GPa] Total indentation work W tot [pJ] Ratio W e /W p [1] Indentation creep C IT [1]
UF-1 36 10.24 ± 2.15 0.63 ± 0.11 44.95 ± 7.49 1.24 ± 0.32 0.14 ± 0.04
UF-1 + 2% P1 37 9.52 ± 1.35 0.59 ± 0.11 45.39 ± 5.21 1.25 ± 0.24 0.14 ± 0.02
UF-2 28 7.56 ± 1.42 0.40 ± 0.09 58.79 ± 8.42 0.77 ± 0.11 0.20 ± 0.02
UF-2 + 2% P1 37 8.39 ± 1.45 0.42 ± 0.03 55.31 ± 2.66 0.79 ± 0.11 0.19 ± 0.01
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W e /W p is the ratio of elastic to plastic deformation work, indentation creep (C IT) was defined as the relative change of the indentation depth while the applied load was kept constant. UF-1, UF-2 pure adhesives, UF-1 + 2% P1, UF-2 + 2% P1 adhesives filled with 2 wt% fibrillated beech pulp (P1)

Results of fracture energy testing

The results of mode I fracture energy testing of adhesive bonds are summarized in Fig. 6. The specific fracture energy determined for unmodified UF showed very clear differences. With a value of 243.2 ± 19.5 J/m² UF-1 yielded a result more than 200% the value of 111.2 ± 27.8 J/m² for UF-2. The specific fracture energy of UF-1 is in a similar order as the specific fracture energy of a melamine-urea–formaldehyde adhesive used for constructive purposes characterized under identical conditions (Veigel et al. in press).

Fig. 6.

Fig. 6

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Specific fracture energy (G Ic) of adhesively bonded joints. Two urea–formaldehyde-(UF)-adhesives were applied without any additional filler (REF) and filled with cellulose nanofibrils from different sources (P1 untreated pulp, P2 TEMPO-oxidized pulp, BC bacterial cellulose). Boxplot symbols: broad line median, box 25–75%-percentile, whiskers minimum and maximum value. The number of specimens tested for each group is given by N

The addition of CNF to UF exerted a number of significant effects on the specific fracture energy of adhesive bonds. Firstly, CNF-reinforced specimens showed higher variability than unmodified specimens on average, perhaps indicating sub-optimal dispersion of fibrils in several cases. Secondly, consistent improvements were only observed with UF-1, whereas significant increases of fracture energy were only sporadically found with UF-2, although a certain trend of improvement with CNF addition is apparent. As confirmed by visual observations during the preparation of the adhesive mixtures and microscopic investigations, large particles of P2 were present after mixing. For this type of cellulose the fibrils could definitely not be dispersed sufficiently well in order to achieve an optimum effect. Based on these observations it can be concluded that fibril dispersion was more efficiently done with UF-1, which comes as a powder, as compared to liquid UF-2.

A detailed analysis of results obtained for UF-1 reveals a clear trend of increasing toughness with increasing content of unmodified fibrils (P1). With a value of 353.0 ± 43.2 J/m², which corresponds to an average increase of 45%, UF-1 reinforced with 2% P1 showed the highest value of specific fracture energy for all tested groups of specimens. To statistically evaluate the effect of added filler, mean specific fracture energy values were compared by one-way ANOVA (p ≤ 0.05). The analysis revealed that four groups of specimens (UF-1 + P1 at a filler content of 1.5 and 2 wt% as well as UF-1 + BC at a content of 0.5 and 1.5 wt%) showed significantly higher values than the unfilled UF-1 reference.

Regarding the three types of filler used in the present study it can therefore be said that it is possible to improve the specific fracture energy of UF-wood adhesive bonds by adding unmodified cellulose nanofibrils (P1) or fibrillated bacterial cellulose (BC), whereas this is not the case for TEMPO-modified cellulose fibrils (P2).

Having established the principal feasibility of improving UF-adhesive bond performance, the question of the cause for this improvement remains to be discussed. Since nanoindentation experiments did not reveal any significant effects of the addition of CNF on the bulk-polymer properties, it is proposed that the positive effect observed is caused by the role that CNF play in the process of crack formation during fracture. As outlined for carbon nanotube-toughened polymers (Mirjalili and Hubert 2010), a significant improvement of the fracture toughness of brittle polymers may be achieved due to fiber-bridging effects, given that the reinforcing fibers are of high tensile strength, above a certain critical length, and show sufficient interfacial adhesion to the polymer.

Conclusions

The results of the present study demonstrate the feasibility of toughening urea–formaldehyde wood adhesive bonds by adding cellulose nanofibrils. The combination of powder urea–formaldehyde with untreated cellulose nanofibrils proved best suitable for this purpose. An increase of the toughening effect up to 45% was observed when adding up to 2% cellulose nanofibrils. The fact that cellulose addition strongly increases the viscosity of the adhesive is a limiting factor to the amount of fibrils that can be added.

Acknowledgments

The authors gratefully acknowledge financial support by the Austrian Science Fund (FWF) under grant P22516. Many thanks go to T. Zimmerman (EMPA) for taking the FE-SEM pictures and C. Tippelreither for his assistance in specimen preparation and mechanical testing.

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