- Original Article
- Open Access
The effect of delignification ratio on the PMMA occupation in poplar wood cell wall by the macro and micro comparative study
Journal of Wood Science volume 69, Article number: 10 (2023)
The polymer/wood functional products may not be true nanocomposites due to the poor permeability of non-polar monomers into the hydrophilic wood cell wall. In this paper, methyl methacrylate (MMA) chosen as the representative non-polar monomer was used to impregnate wood with different lignin removal and then polymerized in situ in delignified wood to obtain polymethyl methacrylate/delignified wood (PMMA/DW). The larger 10 nm mesopores reduction in PMMA/DW-29.9 and the disappearance of the smaller 3 nm mesopores of PMMA/DW-51.7 indicated that the removal of lignin was beneficial for the penetration of MMA in the wood cell wall. When the lignin removal reached between 29.9 and 51.7%, the dimensional stability of PMMA/DW was improved, and it could be speculated that the resin began to enter the wood cell wall at this stage. In addition, the indentation modulus and hardness of the PMMA/DW cell wall were significantly increased when the lignin removal reached 29.9%. This result was consistent with the conclusion of the pore size analysis, which further confirmed that the nanopores of the cell wall were filled with PMMA when the lignin removal was greater than 29.9%. The results of this paper indeed provide a basis for the design of biomass functional nanocomposites.
Wood is a renewable and naturally degradable biomass material. It was ubiquitously used in the construction field for its lightweight, high strength, high modulus, and low thermal conductivity. Unlike other building materials such as steel, cement, and plastics, wood has a unique three-dimensional porous structure with cellulose as the skeleton, lignin, and hemicellulose as filling and cementing substances [1, 2]. Among them, the unique porous structure, microscale, nanoscale hierarchical structure, and pronounced anisotropy give it a series of remarkable characteristics, which provide the possibility for the design of wood-based functional materials [3, 4]. In the past decade, the function of wood has extended to applications beyond construction by optimizing the structure and composition of wood through physical, chemical, or combined modification methods [5, 6]. In recent years, wood-based functional materials have been widely used in many fields, such as the development of high-performance structural materials, energy storage and conversion, environmental remediation, light or thermal management, and so on [7, 8]. A series of products with excellent performance have appeared, such as transparent wood [9,10,11], conductive wood , oil-absorbing wood sponge , wood hydrogel [14,15,16], wood aerogel [17,18,19], ultra-flexible wood [20, 21], and shape memory wood . The increase in the use of wood materials is driven by a variety of factors, including reducing carbon emissions, increasing energy, and supporting sustainable industrialization. However, the high porosity and specific surface area of wood-based templates usually were required to facilitate efficient penetration of polymer monomers when the functional materials were prepared. To further increase the porosity of the wood-based template, there are currently two main solutions. The first is the called “bottom-up” strategy, which uses mechanical or chemical methods to separate the cellulose fibrils in the wood, and then reassemble the separated fibrils to obtain a wood-based template with high porosity [23,24,25]. The other is the so-called “top-down” strategy, which uses chemical methods to remove lignin from wood and retain the original wood frame [26, 27]. The high porosity and specific surface area can be obtained by this method . The “top-down” strategy has many advantages compared with the “bottom-up”, the most typical of which is a simple process and reduced energy consumption . In addition, this method retains the original fiber arrangement in the wood. Compared with the non-directional arrangement structure formed by reassembling after fiber separation, the oriented and ordered structure makes the wood-based template have more excellent mechanical properties.
However, the following problems are still being faced in functional materials manufactured by polymer infiltration to delignification templates. First, wood has a strong polarity because it contains a large number of hydroxyl groups. Many polymers used to make wood-based functional materials tend to have low polarity, which makes them poorly compatible with wood, causing most of the polymer monomers to only fill the wood cell lumen and cannot penetrate the cell wall. Without cell wall penetration, it will be difficult to give full play to the functions and mechanical properties of wood-based functional materials leading to the materials prepared therefrom are not true polymer nanocomposites [28, 29]. In addition, lignin is deposited around cellulose microfibers with a width of 25–30 nm to strengthen the cell wall structure . The removal of lignin will damage the complete structure of wood, resulting in a change of pore structure in wood and a decrease in the elastic modulus and hardness of wood cell walls . The introduction of polymers into the cell wall significantly impacts the physical and mechanical properties of wood-based functional materials.
Methyl methacrylate (MMA) is a common monomer used to make transparent wood based on a delignified template. It has been widely studied because of its refractive index similar to that of cellulose, low price, and simple polymerization process . However, MMA exhibits poor permeability in wood cell walls because of its low polarity. Previous studies have shown that if MMA monomer impregnates wood in liquid form, the polymer only fills the wood cell lumen and cannot be further dispersed in the cell wall . This will not be able to prepare wood-based nanocomposites, which affects the function of wood-based functional materials and limits the improvement of the physical and mechanical properties of the materials. Li et al. used delignified wood as a template and MMA as a filling monomer to prepare transparent wood . The mechanical results showed that transparent wood has better tensile strength than delignified wood and pure polymethyl methacrylate (PMMA), which suggested that the polymer was successfully dispersed in the cell wall. However, this has not been confirmed and the polymer distribution was unknown. Several researchers have used Raman spectroscopy to analyze the distribution of resin in the wood cell wall, and the characteristic functional group –CH2 representing PMMA was discovered. However, the peaks corresponding to –CH2 overlapped with certain chemical components of wood, which increased the difficulty of data analysis . In addition, due to the limited resolution of Raman microscopes, this further reduced the accuracy of PMMA distribution characterization in wood cell walls. Recently, Chen et.al verified that PMMA was distributed in the transparent wood cell wall in nanometer size by small-angle neutron scattering (SANS) technology . The results showed that the pattern of SANS of PMMA/wood biocomposite showed a peak, which indicated that PMMA was distributed in the cell wall in a nanoscale, which confirmed its nanocomposite structure. In addition, the cell wall structure remained inflated due to the use of the solvent exchange method. This allowed PMMA to be distributed not only in the cell wall, but also in the area between cellulose elementary fibrils with a few nanometers in size. This was due to the use of the solvent exchange method to make the MMA monomer impregnation process similar to the natural lignification process.
The polymer/wood functional products may not be true nanocomposites due to the poor permeability of non-polar monomers into the hydrophilic wood cell wall. Therefore, a series of problems may arise, such as the function of polymer/wood composites cannot be well realized, in addition, the dimensional stability and mechanical properties of the composites will also be affected. Herein, we obtained wood templates with different lignin removal by adjusting the chemical treatment time. The delignified wood templates were subsequently impregnated with MMA prepolymer under vacuum, and after two-stage curing, polymethyl methacrylate/delignified wood composites (PMMA/DW) with different lignin removal were obtained. Through cold field emission scanning electron microscope (FE-SEM), attenuated total reflection Fourier infrared spectroscopy (ATR-FTIR), nitrogen adsorption test, volumetric anti-swelling efficiency (ASE), moisture sorption test, dynamic mechanical analysis (DMA) and nanoindentation test, the morphology, permeability, dimensional stability and micromechanical properties of PMMA/DW were explored. Moreover, the effect of lignin removal level on the permeability of MMA in the cell wall was judged. This study provides a strong basis for designing biomass nano-functional composites.
Poplar wood (Populus, L.) were provided by Suqian Hongwei Wood Industry Co., Ltd. (Suqian, Jiangsu, China). Sodium chlorite (NaClO2, 80 wt %), glacial acetic acid (CH3COOH, AR, 99.5%), sodium acetate (CH3COONa, AR, 99%), methyl methacrylate (MMA, CP, molecular weight 100.12, 98%), azobisisobutyronitrile (AIBN, 98%) were purchased from Macleans Biochemical Technology Co., Ltd. (Shanghai, China). The solvents including deionized (DI) water and absolute ethanol were used.
The poplar (Populus, L.) sapwood specimens with 10 mm (longitudinal, L) × 10 mm (tangential, T) × 10 mm (radial, R) were selected for the study. Before chemical treatment, all the samples were dried at (103 ± 2) °C for 24 h until reaching a constant mass (m0) after rinsing with DI and ethanol. The dried samples were then extracted with 2 wt% NaClO2 and acetate buffer solution (pH 4.6) at 80 °C. The different lignin removal specimens were obtained by adjusting the treatment time for 6, 9, 12, 18, and 24 h. The delignified liquid was replaced every 6 h to keep the modification efficient. Subsequently, the extracted samples were soaked in enough distilled water for 12 h to thoroughly remove the residual chemical reagents. After the rinse, the samples were freeze-dried with a vacuum of 20 Pa at − 50 ℃ for 15 h. The specimens were then weighed and recorded as m1 (absolute dry weight) after totally freezing dried. The delignified wood was marked as DW. In addition, for dimensions of 60 mm × 10 mm × 2.5 mm samples, delignified for 2, 4, 6, 9, and 12 h, respectively, were used for the DMA test.
Preparation of PMMA/DW composites
A certain amount of MMA monomer was first weighed and 0.3 wt% AIBN was added. The solution was moved into an Erlenmeyer flask and placed in a water bath at 75 °C for 15 min. Then, the flask was quickly cooled with ice water to prevent an explosion. The DW was put into an impregnation tank and kept under 5 kPa for 30 min to extract air from the wood. Subsequently, the MMA prepolymer was sucked into the impregnation tank and submerged samples. Then the tank was returned to normal atmospheric pressure and kept for 2 h to let the polymer flow into the samples. Next, the impregnated specimens wrapped in the aluminium foil were kept at (75 ± 2) °C for 4 h after removing the excess monomer and then were heated up to (105 ± 2) °C to fully solidify the prepolymer until the weight was constant. After removal from the oven, the samples were weighed and recorded as m2 (absolute composite dry weight).
The lignin content of the original wood and DW was determined according to GB/T 747–2003 Pulps—determination of acid-insoluble lignin. Firstly, the specimens were extracted by Soxhlet extractor with the benzene–alcohol mixture (volume ratio 2:1) for 6 h. Secondly, they were placed in a 250 ml Erlenmeyer flask after being air-dried and the pre-prepared (72 ± 0.1) % sulphuric acid solution was added with shocking. The process was kept for 2 h at 20 °C. Thirdly, all the contents in the 250-ml Erlenmeyer flask were transferred into a 2000-ml Erlenmeyer flask and the acid concentration was diluted to 3% with distilled water. The insoluble matter was precipitated after being boiled for 4 h. After that, the deposits were filtered and washed with hot distilled water until they showed neutral. Finally, the filter paper and residue were moved into a weighing bottle and dried in an oven at (105 ± 3) °C to a constant weight to measure the acid-insoluble lignin (m). The acid-insoluble lignin content X (%) was calculated according to Eq. 1:
where m is the weight of the completely dried acid-insoluble lignin and m1 is the weight of the completely dried natural wood and DW.
The oven-dried mass and volume of the specimens were measured to calculate the density and weight percent gain (WPG) using 10 replicates. The WPG was calculated according to Eq. 2:
where m2 is the oven-dried weight of the composite PMMA/DW and m1 is the totally dried weight of DW.
The micro-morphology of the original wood, DW, and PMMA/DW was investigated by a cold field emission scanning electron microscope (JSM-7600F, JEOL Ltd.) under an accelerating voltage of 3 kV, and the cross-sectional surface of the sample was cut using an ESM-150 s slide microtome (Elma, Japan). ATR-FTIR spectra of the samples were recorded on a VERTEX 80 V spectrometer (Bruker, Germany) over the scan range of 400–4000 cm−1. The surface area and pore size distribution were analyzed by the nitrogen adsorption device (ASAP 2020 HD88, Micromeritics, USA) at 77 K. Before the measurements, samples were out-gassed at 100 ℃ for 6 h to remove the water vapor. The specific surface area (SBET) was calculated according to the Brunauer–Emmett–Teller method (BET). The pore size distribution was determined by the Barrett–Joyner–Halenda (BJH) method.
The dimensional stability of the natural wood and PMMA/DW were determined according to GB/T1932.2-2009 Method for determination of the swelling of wood. Firstly, the samples were dried at 60 °C until reaching a constant dimension. Then, the samples were placed at a temperature of (20 ± 2) °C and a relative humidity of (65 ± 3)% to absorb moisture until dimensionally stable. During the moisture absorption process, the size change along the grain direction was measured every 6 h and the size was considered to be stable when the difference between the two measurement results did not exceed 0.1 mm. Finally, the samples were immersed in distilled water up to the time their size stabilized. The method of checking whether the sample size has been stable was similar to the moisture absorption process except for a 0.01 mm measurement change. The swelling coefficient (α) and anti-swelling efficiency (ASE) can be calculated by Eqs. 3–6:
In the formula, α65% represents the volumetric swelling coefficient of the sample at 65% RH; αmax represents the volumetric swelling coefficient of the sample when it is saturated with water. V0, V65%, and Vmax are the volume of the sample when it is absolutely dry, absorbs moisture, and absorbs water to dimensional stability, respectively. ASE65% and ASEmax are the volumetric anti-swelling efficiency of moisture absorption and water absorption, respectively. α65%(C) and α65%(P) are the volumetric swelling coefficient of natural wood and PMMA/DW under moisture absorption, respectively. αmax(C) and αmax(P) are the volumetric swelling coefficient of natural wood and PMMA/DW under water absorption, respectively.
The dynamic mechanical analysis (DMA) of the control and PMMA/DW samples were conducted by the Q800 (TA, US) in the double cantilever beam mode. The samples with dimensions 60 mm × 10 mm × 2.5 mm (L × T × R) were scanned over a range of 30 to 250 ℃ with an increased speed of 3 ℃/min and frequency of 2 Hz. The micromechanical properties of wood cell walls were evaluated by nanoindentation (iMicro, Nano Force, US) with 5 mm × 5 mm × 5 mm (L × T × R) samples, the surface of samples was processed by Leica ultracut R-type ultrathin slicer (Leica, Germany). The samples were all placed at 20 °C and 65% relative humidity for 48 h before the test. The maximum load tested was 400 μN and the loading and unloading rates were both 80 μN/s. The load was maintained for 5 s when it reached the maximum. The indentation modulus and hardness of the cell wall were calculated according to the research of Tze et al. .
Results and discussion
Lignin removal process
Figure 1 shows that the wood color changed with the extension of the delignification duration. It changed from brown to yellow and finally to white with different process times. The reasons for the radical transformation in color are that lignin is the main light-absorbing component in wood and there are many chromophoric groups in lignin structure such as carbonyl groups, carboxyl groups, and alkene conjugated with benzene rings [36, 37]. In addition, there are many auxochrome groups such as phenolic hydroxyl and alcoholic hydroxyl. These chromophoric and auxochromic groups present in the structure of lignin are the main foundation of wood color. Table 1 shows lignin content changes of modified wood and the corresponding lignin removal level. More lignin in the wood cell wall was taken away as the modification time was prolonged. The lignin content was reduced and the structure was destroyed resulting in a color alternation.
Figure 2a is the schematic diagram of the preparation of PMMA/DW and FE-SEM photos of original wood, delignified wood with 97.3% lignin removal (DW-97.3) and PMMA filled 97.3% delignified wood (PMMA/DW-97.3) are shown in Fig. 2b–d, respectively. It could be seen from Fig. 2b that wood fiber cells were mainly composed of empty cell lumens and solid cell walls. The cell wall is composed of substantial materials which provide the basis for the density and mechanical properties of wood . The space between adjacent wood fiber cell walls contains the middle lamella and the cell corner, both of which have very high lignin content [39, 40]. It can be observed from Fig. 2c that there were obvious gaps in the intercellular layers between the cell walls and the cell corners after the delignification treatment. In addition, the rough structure of the cross-section of the cell wall could be easily observed with greater magnification. Nano-scale pores appeared on the secondary wall, which was consistent with previous research results about the microstructure of DW . Figure 2d shows that almost all wood cell lumens were filled with PMMA and the pores created by the chemical treatment in the intercellular layer and cell wall corners were also almost fully occupied. Compared with DW-97.3, the cell wall of PMMA/DW-97.3 become smooth and the nanoscale pores on the secondary wall were also filled. Nevertheless, the degree of filling at the micro- and nano-levels needs to be further explored. In most cases, it is not necessary to remove almost all lignin when designing related functional composite materials that are time and energy-consuming and environmentally unfriendly.
The WPG and density of PMMA/DW are shown in Fig. 3. When the lignin removal level was lower than 29.9%, the WPG of PMMA/DW was 110 wt% with no significant difference among the 0, 17.4, and 29.4% groups. When the removal level reached 51.7%, the WPG increased to 125%, which was significantly higher than the wood with less delignification. After that, WPG still increased with further lignin removal. This was mainly due to the appearance of more void space in the wood cell walls as the lignin was removed, which facilitated the penetration and solidification of plastic in the cell wall. In addition, when the lignin removal percentage attained 51.7%, the density of the composite material increased from the original 0.47 g/cm3 to 0.95 g/cm3, an increase of 102%. Subsequently, the density of PMMA/DW went on climbing with more serve delignification. The density of PMMA/DW come up to 1.15 g/cm3 when the lignin removal level achieved 97.3%, which was almost the same as the density of pure PMMA .
The lignin removed from the original wood was also confirmed by FTIR analysis (Fig. 4). The characteristic bond at 1593, 1505 (lignin aromatic ring C=C stretching vibration) and 1462 cm−1 (aromatic skeleton vibration) of lignin disappeared gradually after prolonged delignification chemical treatment. The characteristic bond of hemicellulose at 1736 cm−1 and cellulose at 896 cm−1 was retained in all samples, confirming the process selectivity for lignin removal.
Nitrogen adsorption was used to analyze the pore size and PMMA distribution in wood cell walls. The nitrogen adsorption and desorption isotherms of original wood, DW, and PMMA/DW are shown in Fig. 5. Obviously, the DW could absorb more nitrogen and the nitrogen adsorption capacity gradually increased with the processing degree upraised (Fig. 5a). After being plastic impregnated and solidified, the adsorption of nitrogen was greatly reduced (Fig. 5b). In addition, hysteresis was obvious in all DW samples while in the polymer-impregnated DW was very limited. Figure 6a shows the pore size distribution in the range of 2–18 nm of natural wood and DW and the accumulative pore volume in the wood cell wall. The peak appeared at about 3 nm in the original wood indicating that there were more mesopores in this diameter range, which was similar to the results of previous research . The number of mesopores around 3 nm increased with delignification, as shown by the increased intensity of the peak there. The heightening in the specific surface area and total pore volume of DW with delignification in Table 2 also confirmed the transformation of the number of mesopores and pore diameters caused by “top-down” delignification. Comparing Fig. 6a and b shows the change in pore size and volume when PMMA was added. Based on PMMA/DW-0, PMMA/DW-17.4 had an obvious peak at 10 nm and PMMA/DW-29.9 had a weaker peak at 10 nm. Furthermore, when the lignin removal level was lower than 29.9%, the peak at 3 nm remains, suggesting that the PMMA distribution efficiency in smaller 3-nm mesopores was greatly lower than in the larger 10-nm mesopores. As lignin removal increased, the 3-nm peak almost disappeared.
The above results revealed that when the lignin removal was lower than 29.9%, the PMMA distribution efficiency in smaller mesopores was greatly lower than that in larger mesopores. Here were the pores of 3 nm and 10 nm, respectively, when the lignin removal exceeded 29.9%, the PMMA distribution efficiency in the two mesopores showed the opposite pattern. After PMMA occupied the cell wall, the number of mesopores in DW within 29.9–51.7% lignin removal was reduced. When lignin removal reached 97.3%, all the mesopores detected in this study disappeared. In combination with Table 3, it could be seen that delignification promoted the distribution of PMMA in the wood cell wall pores. When the lignin was almost completely cleared away, all the mesopores in the cell walls were charged with PMMA. The natural pores enlarged to the diameter of 3–4 nm mixed in the cellulose microfibrils due to the removal of lignin were unveiled to the non-polar monomers. After being impregnated with polymer, not only commonly known cell cavities but also cell wall pores were refilled. The results confirmed that PMMA was distributed in the transparent wood cell wall on the nanoscale using the small-angle neutron diffraction technique in the case of large lignin removal by Chen et al. . But under the situation of insufficient lignin removal work, the non-polar monomer plastic polymer can hardly enter the common target cell walls.
To explore the influence of PMMA impregnation on the dimensional stability of DW, the volume-swelling coefficient and anti-swelling efficiency of the samples were also analyzed here. As shown in Fig. 7a, the results showed that the α65% and αmax of PMMA/DW-0 were significantly reduced compared to the natural wood. Corresponded ASE65% and ASEmax of the PMMA/DW-0 reached 29.34% and 37.03%, respectively. Figure 7b shows that the combination of PMMA and wood effectively reduced the moisture absorption and water absorption of wood. However, the α65% and αmax of the PMMA/DW began to increase with the delignified process. The ASE65% and ASEmax of PMMA/DW-17.4 were significantly reduced, which was due to the partial removal of lignin causing the cell wall to expose more hydrophilic hydroxyl groups to the water . Interestingly, α65% and αmax of PMMA/DW decreased when the lignin removal reached 29.9%. This phenomenon can be assumed to be because when the lignin removal exceeds 29.9%, the resin begins to penetrate the cell wall and polymerize in situ to generate PMMA. The absorption of water by the hydroxyl group was hindered molecularly due to the distribution and occupation of PMMA in the nanopores of the cell wall, thereby inhibiting the change in the cell wall size. Furthermore, the α65% and αmax of PMMA/DW continued to decrease and the corresponding ASE65% continued to improve thereafter. This was owing to more polymer joining the cell wall and filling the nanostructure pores. This was consistent with the above result of pore-size distribution showing the number of 10 nm pores in PMMA/DW decreased when the lignin removal reached 29.9%. When the lignin removal reached 51.7%, the mesopores with a diameter of about 3 nm disappeared. This phenomenon may be due to the further penetration of plastics and the filling of nanopores in the cell wall. This also explained why the ASE65% and ASEmax of PMMA/DW-51.7 continued to increase. However, α65% and αmax of PMMA/DW were successively increased as the lignin removal continued to increase. Correspondingly, ASE65% also decreased obviously and ASEmax even had a negative value. This was probably attributable to the increasing proportion of PMMA in the composite system as the degree of chemical treatment enhanced and the original strong chemical bond in the composite system was replaced just by more physical filling. This might exacerbate the interface separation between cellulose and PMMA and ultimately led to poor dimensional stability.
Dynamic mechanical properties
As shown in Fig. 8a, the storage modulus E’ of the natural wood and PMMA/DW decreased with the increase in temperature owing to the increase in the fluidity of the high molecular polymer in the wood. The E’ of the original wood decreased significantly at about 220 °C. The flexibility increase of the amorphous part of wood undertook relevant local responsibilities. The appearance of this phenomenon was mainly caused by the micro-Brownian motion of the molecular chains of the cellulose amorphous region . The E’ of PMMA/DW-0 at room temperature increased to 9887 MPa from 8798 MPa of the original wood, which showed that the PMMA filling only in the cell lumen could effectively improve the elasticity of wood. However, the E’ of PMMA/DW gradually decreased when the lignin removal rose. As a filling matrix for the cell wall, lignin can fix the cellulose molecular chains and hinder their free movement. When the lignin content of the cell wall was reduced, it was easier for the slippage to occur among the cellulose macromolecule chains, which directly caused the rigidity of the wood to drop. However, PMMA only filled DW in a separate form, which did little to improve the stiffness of the composite. The E’ of PMMA/DW-97.3 increased when the lignin removal reached 97.3%. This was owing to the plastic fully penetrating the cell wall, more nanoscale pores being filled and the molecular weight of PMMA gradually increasing, thereby the rigidity was improved.
Figure 8b shows the relationship between the loss tangent (tanδ) of the wood and temperature. The tanδ of the natural wood and PMMA/DW increased with the temperature raising. This was because the viscosity of the polymer in the wood increased with the heightening of temperature and the transition from elasticity to viscosity was a typical feature of wood viscoelasticity . When the lignin removal reached 29.9%, the tanδ increased significantly at 130 °C which was the glass transition temperature corresponding to PMMA . When the lignin removal surpassed 51.7%, the tanδ remained at the maximum level. It meant that the proportion of PMMA in the PMMA/DW system further increased as the lignin removal rose. Besides, the tanδ of PMMA/DW increased overall as the lignin removal level improved. This was owing to more pores being created in the cell wall as the lignin was removed, which facilitated the penetration and aggregation of plastic in the cell wall and replaced the original lignin. The combination method of cell wall components changed from the original chemical combination between cellulose and lignin to the current physical combination between cellulose and PMMA. The degree of cross-linking between the cellulose molecular chains was further reduced, so there would be more energy loss when the molecular chains moved. This leads the tanδ of PMMA/DW to improve more.
Micromechanical properties of the natural wood and PMMA/DW cell walls were investigated by nanoindentation. Hardness, indentation modulus, and typical indentation load–depth curves of the cell wall are presented in Fig. 9, respectively. Compared with the original wood, the hardness and indentation modulus of PMMA/DW-0 were unchanged (Fig. 9d, e). This indicated that PMMA only loaded in the cell lumen and had not yet been seeded in the cell wall. The hardness and indentation modulus of PMMA/DW-17.4 were reduced by 22.92% and 6.14% compared with PMMA/DW-0, respectively. When the lignin removal got 29.9%, the hardness and indentation modulus of PMMA/DW-29.9 began to increase. Since then, the hardness and indentation modulus of PMMA/DW also improved as the delignification process was promoted. After almost all lignin had been taken away, the hardness and indentation modulus of PMMA/DW-97.3 increased by 38.54% and 81.76% compared with PMMA/DW-0, respectively. The above results indicated that when the degree of delignification was light, the hardness and indentation modulus of the cell wall tended to go down because partial lignin was removed and the polymer had not moved into the cell wall by the common processing conditions. When the lignin removal exceeded 29.9%, the Nanoindentation tested hardness and indentation modulus of the cell wall increased significantly (P < 0.05). This owed to the Nano field porosity of the wood cell wall increased as the lignin was further removed and made the polymer combined with the cell wall in the nanoscale. This promoted the penetration of MMA in the cell wall. After that, more MMA resided and polymerized in the cell wall Nano voids which gifted the cell wall more excellent mechanical properties.
Based on the poor permeability of non-polar monomers such as MMA in the delignification template, may cause the bad dimensional stability and mechanical properties of wood-based functional materials. In this paper, MMA was used to impregnate the wood with different lignin removal ratios; and then polymerized in situ to obtain PMMA/DW. The WPG results showed that the removal of lignin was beneficial to increase the weight of PMMA/DW, and the density of PMMA/DW also improved. When the lignin removal reached 97.3%, the density of PMMA/DW-97.3 was 1.15 g/cm3, which was the same density as pure PMMA. The results of nitrogen adsorption showed that the number and diameter of mesopores with 3 nm pore size of wood increased with the raise of lignin removal. When the lignin removal reached 29.9%, the number of mesopores with a 10 nm pore diameter of PMMA/DW-29.9 gradually reduced, indicating that resin penetrated the cell wall in this diameter range. When the lignin removal reached 51.7%, all mesopores with a pore size of 3 nm of PMMA/DW-51.7 disappeared, revealing that plastic was distributed in smaller mesopores in the cell wall. The reduction of PMMA/DW-29.9 of the larger mesopores and the disappearance of PMMA/DW-51.7 of the smaller mesopores further indicate that the removal of lignin is beneficial to the penetration of polymer in the wood cell wall. The subsequent increase in ASE65% and ASEmax of PMMA/DW-29.9 and PMMA/DW-51.7 confirmed that the filling of plastic on the cell wall nanopores improved the dimensional stability of wood. DMA results showed that the storage modulus of PMMA/DW generally decreased with the exchange of PMMA and lignin in wood, which was caused by the poor combination of non-polar monomer polymer and wood polar components. The nanoindentation results show that when the lignin removal reached 29.9%, the indentation modulus and hardness of the PMMA/DW cell wall significantly increased, which indicated that plastic was uniformly dispersed in the cell wall and the mechanical properties of the cell wall were remarkably improved. The significant enhancement of the cell wall mechanical properties at a lignin removal of 29.9% determined that the delignification level regarding the occupation of non-polar resin in the wood cell wall was 29.9%. This study takes MMA as the research object to provide data for the dispersibility of non-polar monomers in delignified wood, as well as a reference for the dimensional stability and mechanical properties of such polymer/wood-based functional materials.
Availability of data and materials
All data discussed during this study are included in this published article.
Polymethyl methacrylate/delignified wood
Weight percent gain
Field emission scanning electron microscope
Attenuated total reflection Fourier infrared spectroscopy
- SBET :
Specific surface area
- α 65 % :
Volume swelling coefficient of moisture absorption
- α max :
Volume swelling coefficient of water absorption
- ASE65% :
Volumetric anti-swelling efficiency of moisture absorption
- ASEmax :
Volumetric anti-swelling efficiency of water absorption
Dynamic mechanical analysis
- tan δ :
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Thanks to “the Advanced analysis and testing center of Nanjing Forestry University” for the professional and thoughtful testing services.
This work was financially supported by the National Natural Science Foundation of China (31870543) and the Youth Science and Technology Innovation Fund of Nanjing Forestry University (cx2016017).
The authors declare that they have no competing interests.
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Zhang, H., Xu, F., Xu, L. et al. The effect of delignification ratio on the PMMA occupation in poplar wood cell wall by the macro and micro comparative study. J Wood Sci 69, 10 (2023). https://doi.org/10.1186/s10086-023-02082-5
- Wood composite
- Cell wall