Next Article in Journal
The Structure and Properties of Polyacrylonitrile Nascent Composite Fibers with Grafted Multi Walled Carbon Nanotubes Prepared by Wet Spinning Method
Previous Article in Journal
Morphology Control in a Dual-Cure System for Potential Applications in Additive Manufacturing
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Polymers
Volume 11
Issue 3
10.3390/polym11030421
polymers-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Magnetic Properties of FeNi3 Nanoparticle Modified Pinus radiata Wood Nanocomposites

by
LiLi Wang
*,
Na Li
,
Tiqi Zhao
,
Bin Li
and
Yali Ji
College of Science, Northeast Forestry University, Harbin 150040, China
*
Author to whom correspondence should be addressed.
Polymers 2019, 11(3), 421; https://doi.org/10.3390/polym11030421
Submission received: 29 January 2019 / Revised: 23 February 2019 / Accepted: 1 March 2019 / Published: 5 March 2019
(This article belongs to the Special Issue Towards Functional and Structured Smart Polymeric Systems)
Browse Figures
Review Reports Versions Notes

Abstract

:
Magnetic FeNi3 nanoparticles were synthesized in the internal structure of wood through an in situ fabrication approach. The morphology, crystalline phase and chemical composition of the FeNi3 modified wood was investigated by X-ray powder diffraction (XRD), Fourier transform infrared (FTIR) spectroscopy, scanning electron microscopy (SEM) with energy-dispersive X-ray (EDX) analysis and X-ray photoelectron spectroscopy (XPS). SEM confirmed that the magnetic nanoparticles were densely dispersed in the wood matrix. The magnetic hysteresis loops showed that the magnetism of composites is dependent on the amount of FeNi3 loading. The saturation magnetization of magnetic wood increases from 6.3 to 10.8 emu/g with an increase of FeNi3 loading from 12 to 18 wt %. Furthermore, magnetic wood showed significant directional dependence. The presented work will provide a feasible pathway for producing wood composite products.

Graphical Abstract

1. Introduction

Wood is a structured and ordered natural polymer material, which has excellent hierarchical structures and physical properties due to its natural growth [1]. It is used in several important engineering applications, such as interior decoration, building materials and in furniture industry. Furthermore, wood with a microporous structure can combine a natural porosity scaffold with inorganic/organic compounds. Therefore, many efforts have been devoted to creating functionalized wood by dispersing inorganic and organic components into the wood matrix in order to endow these wood-based materials with new properties, such as biodegradation resistance [2], rheological properties [3], mechanical properties [4,5,6], acoustic properties [7], and magnetic properties [8]. Among these properties, magnetism has recently received much attention.
Magnetic wood is a composite that exhibits the inherent lightweight properties of the wood substrate and the magnetic properties of nanoparticles, which achieves a good harmony between both wood and magnetism [9]. Thus, magnetic wood has potential applications in electromagnetic shielding, as an indoor electromagnetic wave absorber, as a heating board and for heavy metal adsorption [10,11,12,13]. So far, studies on magnetic wood have mostly focused on ferrite particle modified wood, such as Fe3O4 [14], CoFe2O4 [15], MnFe2O4 [16] and so on. Fe, Ni and their alloys are very important soft magnetic materials due to their higher saturation magnetization and smaller coercive forces when compared with ferrites [17,18,19,20]. Furthermore, they have a wide range of applications, such as acting as electromagnetic wave absorbers, transformers, magnetic sensors and magnetic recording heads [21,22].
When the molar ratio of Fe to Ni is 1/3, the FeNi3 intermetallic compound can be obtained. Lu et al. reported that ferromagnetic FeNi3 nanoparticles have been successfully synthesized via a hydrazine hydrate reduction in aqueous solution at room temperature. Furthermore, the saturation magnetization reaches about 110 emu/g [23]. In addition, Yuan et al. reported that the FeNi3 alloy was prepared using hydrazine hydrate as a reducing agent in strong alkaline media. The saturation magnetization of FeNi3 alloy is 48.48 emu/g [24]. However, FeNi3 nanoparticle modified wood composites have not been reported until now. Hydrazine hydrate is a low-cost moderate reducing agent and has been proven to be good alternative to produce FeNi3 metallic particles. Therefore, in this study, FeNi3 nanoparticles were formed in the cell cavity of wood using hydrazine hydrate as a reducing agent through a simple in situ synthesis. The morphology, chemical composition and magnetism of the obtained modified wood composites was investigated.

2. Materials and Methods

2.1. Materials

P. radiata pine specimens were cut into blocks of 20 mm (longitudinal) × 20 mm (radial) × 10 mm (tangential) and dried in a vacuum oven (DHG-9203A, Shanghai, China) at 60 °C for 12 h to a constant weight. All the reagents in the experiment were analytical grade and used without further purification. Ferrous ammonium sulfate hexahydrate ((NH4)2Fe(SO4)2·6H2O), nickel sulfate hexahydrate (NiSO4·6H2O), sodium hydroxide (NaOH), hydrate hydrazine (N2H4·H2O, 80%) and absolute ethanol (C2H5OH) were purchased from the Tianjin Kemiou Fine Chemical Reagent Co. (Tianjin, China). Deionized water (Milli-Q Academic, Beijing, China) was exclusively used in all aqueous solutions and rinsing.

2.2. Preparation of FeNi3 Nanoparticle Magnetic Wood Composites

The mixture of (NH4)2Fe(SO4)2·6H2O and NiSO4·6H2O with a molar ratio of 1/3 was dissolved in 50 mL distilled water to form three homogeneous solutions: A, B and C, respectively. Mixed solution A, with a concentration of 0.6 mol/L, contains 2.94 g (NH4)2Fe(SO4)2·6H2O (0.0075 mol) and 5.91 g NiSO4·6H2O (0.0225 mol). Mixed solution B, with a concentration of 0.8 mol/L, contains 3.92 g (NH4)2Fe(SO4)2·6H2O (0.01 mol) and 7.88 g NiSO4·6H2O (0.03 mol). Mixed solution C, with a concentration of 1.0 mol/L contains 4.90 g (NH4)2Fe(SO4)2·6H2O (0.0125 mol) and 9.86 g NiSO4·6H2O (0.0375 mol). Firstly, the wood specimens were entirely dipped into solutions A, B, and C under a lowered pressure of 0.09 MPa for 2 h, respectively. NaOH (2 g) and hydrazine hydrate (9.0 mL) were added in 50 mL distilled water to form an alkaline hydrate hydrazine solution. Subsequently, the above pretreated wood samples were rapidly soaked into the alkaline hydrate hydrazine solution with a mole concentration of 3 mol/L at 70 °C for 6 h. The formed nanoparticles were labeled as FeNi3. Finally, FeNi3 modified magnetic wood composites were washed with distilled water and absolute ethanol three times and dried in a vacuum drying oven at 60 °C.
The weight percent gains (WPGs) (%) of the wood samples after treatment were calculated by the following equation:
WPG (%) = (W1 − W0)/W0 × 100 %
Where W0 and W1 are the weights of the oven dried wood before and after treatment, respectively.
The WPGs for the three modified wood samples were 12, 15 and 18 wt % at 0.6, 0.8 and 1.0 mol/L ion concentrations of the precursor solution, respectively. Thus, the resulting specimens of the modified wood were labelled as MW–12 wt %, MW–15 wt % and MW–18 wt %, respectively. Furthermore, the experimental scheme for the preparation of the FeNi3 nanoparticle modified wood is displayed in Figure 1.

2.3. Characterization Techniques

The morphology of the unmodified wood and modified wood composites was observed through scanning electronic microscopy (SEM, Quanta 200, FEI Company, Eindhoven, Holland). Chemical compositions of the FeNi3 modified wood composites were detected by energy-dispersive X-ray spectroscopy (EDX, EDAX Inc., Mahwah, NJ, USA). The crystalline structure of unmodified wood and modified wood were identified using the X-ray diffraction technique (XRD, D/MAX–3B, Rigaku, Tokyo, Japan), using Cu Kα radiation (λ= 1.5418 Å), a generator operated at 1,200 W (40 kV× 30 mA), and a 2θ scan range from 10° to 80°, with a scanning speed of 4°/min. For the Fourier transformation infrared (FTIR, Thermo Nicolet, Madison, WI, USA) spectroscopy, thin sample disks were separately made by grinding small portions of the wood specimens and pressing them with potassium bromide, then the spectra of the unmodified and modified wood were obtained, with a scanning range of 4000–500 cm−1 at a resolution of 4 cm−1. X-ray photoelectron spectroscopy (XPS, K–Alpha, Thermo Fisher Scientific Company, Waltham, MA USA) was used for the surface analysis of the chemical composition of modified wood. The hysteresis loops of the samples were investigated using a vibrating sample magnetometer (VSM, MPMS–XL–7, Quantum Design Company, San Diego, USA) with a maximum applied magnetic field of 10,000 Oe at room temperature (about 300 K).

3. Results and Discussion

3.1. XRD Analysis of Unmodified and Modified Wood

Figure 2a–d shows the XRD patterns of the unmodified wood and the three modified wood samples, respectively. From Figure 2a, the diffraction peaks of the unmodified wood at 16° and 22° correspond to crystal planes (101) and (002) of cellulose, respectively [25]. For all of the modified woods, these characteristic peaks of pristine wood are distinctly weakened, shown in Figure 2b–d, which is due to the deposited metal particles destroying the crystalline structure of the cellulose, resulting in a decrease in the crystalline structure of the cellulose. Moreover, characteristic peaks at 2θ values of 44.3°, 51.7° and 75.8° correspond to the crystal planes of (111), (200), and (220) of the FeNi3 particles, respectively [26]. This is the typical diffraction pattern of a face-centered cubic (FCC) phase (JCPDS No. 38–0419). Meanwhile, the WPGs of the magnetic wood composites increase from 12 to 18 wt % with an increase of ion concentration from 0.6 to 1.0 M. This indicates that the ferrous and nickel ion concentrations can control the content of the FeNi3 nanoparticles in the wood composites. Thus, the intensity of the diffraction peak increases obviously with the increase of FeNi3 loading. The above analysis indicates that FeNi3 particles with high crystallinity and homogeneity are successfully prepared in wood.

3.2. FTIR Analysis of Unmodified and Modified Wood

Figure 3 shows the FTIR spectra of unmodified wood and MW–18 wt %. For the unmodified wood, a strong O–H stretching absorption at 3430 cm−1 is observed. The bands at 2930, 1730, 1650 and 1510 cm−1 are attributed to the stretching vibration of C–H in CH3, stretching vibrations of C=O in hemicelluloses, stretching vibrations of conjugated carbonyl and aromatic stretching vibrations of lignin, respectively [27,28,29]. For the modified wood, the characteristic absorption bands of wood have changed when compared with the unmodified wood. The bands at around 1730 cm−1 have disappeared because of the degradation of acetyl groups in hemicelluloses by magnetic treatment [30]. Meanwhile, the O–H stretching absorption band at 3430 cm−1 have shifted to a lower wavenumber, 3400 cm−1, confirming that the interactions occurred between the OH groups of the wood matrix and the formed FeNi3 nanoparticles through hydrogen bonds [31]. A new characteristic band at 611 cm-1 is attributed to O–Fe and O–Ni stretching modes [32,33]. Moreover, the bands intensities at around 1590 cm−1 and 1440 cm−1 were significantly enhanced, which can be attributed to chemical bonding between the surface-active hydroxyl groups of the FeNi3 nanoparticles and the carboxyl groups of the wood [34].

3.3. Morphology Analysis of Unmodified and Modified Wood Composites

Figure 4a–d shows the SEM images of longitudinal cross-sections of the unmodified wood and MW–18 wt %. From Figure 4a, it can be seen that the unmodified wood has microgrooved structures and smooth lumen walls. However, the modified wood composites show that the microgrooved structures of the original wood have been covered by modified particles, as seen in Figure 4b. This reveals that the FeNi3 particles are adhering to the lumen walls of the wood. As shown in Figure 4c, a large amount of FeNi3 particles are deposited together continuously and appear as a densely deposited layer. Figure 4d indicates that the morphology of the FeNi3 nanoparticles is a rounded disk, with diameter of about 100 nm. The above SEM tests confirm that the FeNi3 nanoparticles are imbedded into the inner cavity of wood by in situ chemosynthesis. Figure 5 shows the energy-dispersive X-ray (EDX) analysis of the modified wood. It illustrates that the atomic ratio of iron to nickel is 1:2.70, which is close to the initially set ratio of 1:3.

3.4. XPS Analysis of Unmodified Wood and MW–18 wt % Composite

Figure 6a,b show wide scan XPS spectra for the unmodified wood and MW–18 wt %, respectively. The major elements for the unmodified wood are C and O, as seen in Figure 6a. The peaks at 285.3 and 530.6 eV are attributed to C 1s and O 1s, respectively. Moreover, C, O, Ni and Fe elements were detected in the modified wood, as seen in Figure 6b. Figure 6c shows the XPS spectrum of the Fe 2p of the modified wood. The binding energy for the 2p3/2 peak of iron (Fe0) is around 706.5 eV. Furthermore, peaks centered at 709.20, 722.41, 711.14 and 724.45 eV are 2p3/2, 2p1/2 of Fe2+ and 2p3/2, 2p1/2 of Fe3+, respectively [35].
Figure 6d shows the XPS spectrum of Ni 2p. The binding energy at 852.4 and 870.0 eV is 2p3/2 and 2p1/2 of Ni0 [36]. Peaks at 855.2 and 872.8 eV are assigned to 2p3/2 and 2p1/2 of Ni2+, respectively. The binding energy at 862.0 and 878.7 eV corresponds to satellite features of 2p3/2 and 2p1/2 of Ni2+ [37]. The above XPS results demonstrate that Ni2+ and Fe2+ have been well reduced to Fe0 and Ni0. Furthermore, a part of the oxidation states of Ni and Fe elements is observed in XPS. The reason for this is that the oxidation of Ni and Fe elements on the surface of wood composites with a depth of several nanometers is unavoidable at atmospheric conditions [38].

3.5. Magnetism Analysis of Composites

Figure 7a shows the magnetic hysteresis loops of the modified wood composite at room temperature. It is obvious that all the composites exhibit a typical hysteretic behavior. The saturation magnetization varies with the applied magnetic field. Magnetic wood composites with FeNi3 loading of 12, 15 and 18 wt % possess saturation magnetizations of 6.3, 8.1 and 10.8 emu/g, respectively. This result points out that higher FeNi3 loading in the wood matrix would better increase the saturation of magnetization. Furthermore, the saturation of magnetization of FeNi3 modified wood composites is higher than iron oxide-modified thermoplastic wood materials [39] and CoFe2O4-modified wood composites [40]. Further, it is observed that the coercive forces of modified wood are about 45 Oe, which indicates that these modified wood composites display a soft magnetism behavior [41]. However, the saturation of magnetization of the FeNi3 modified wood composites is obviously lower than the FeNi3 nanoparticles (110 emu/g and 48.48 emu/g, respectively) [23,24]. The reason for this is that the wood leads to a magnetically dead layer [42].
Since the native biomaterial wood possesses intrinsic anisotropy [43], whether the MW–18 wt % wood fiber directions were parallel or vertical to the applied magnetics direction was compared. As shown in Figure 7b, when the wood fiber was parallel to the external magnetic field, the magnetic hysteresis loops were significantly steeper, suggesting that it is easier to be magnetized this way. Because the magnetic particles were mainly deposited along the longitudinal fiber growth direction, the fiber orientation will influence the magnetic properties [44]. Thus, the result indicates that the magnetism of FeNi3 nanoparticle modified wood shows directional dependence, which is similar to the ferrite loaded wood reported before [45].
Figure 8 shows the excellent magnetic property of the modified wood. The magnetic wood can be firmly attracted and easily lifted by a permanent magnet, as seen in Figure 8a. The wood specimen can be observed floating on the surface of the water in Figure 8b. The wood can overcome the buoyancy of the water and be attracted to the bottom of the cup by using the external magnet, as demonstrated in Figure 8c.

4. Conclusions

In summary, magnetic wood composites with different saturations of magnetization were fabricated by in situ chemosynthesis. The FeNi3 nanoparticles were successfully synthesized in the wood matrix. Magnetic wood composites exhibit better a saturation of magnetization, with an increase in FeNi3 content. The fiber orientation in the wood structure has a certain influence on the magnetic characteristics. The presented approach provides a method for producing inexpensive, lightweight and soft magnetic wood composites.

Author Contributions

The author L.W. conceived and designed the experiments; L.W. and T.Z. analyzed the data and wrote the paper; T.Z., N.L. and Y.J. performed the experiments; and B.L. contributed the data analysis work and revision of this paper.

Funding

This study was financially supported by the Fundamental Research Funds for the Central Universities (No. 2572017CB24), and the Postdoctoral Scientific Research Starting Foundation of Heilongjiang Province (No. LBH-Q17004).

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Ugolev, B.N. Wood as a natural smart material. Wood Sci. Technol. 2014, 48, 553–568. [Google Scholar] [CrossRef]
  2. Lykidis, C.; Bak, M.; Mantanis, G.; Németh, R. Biological resistance of pine wood treated with nano-sized zinc oxide and zinc borate against brown-rot fungi. Eur. J. Wood Wood Prod. 2016, 74, 909–911. [Google Scholar] [CrossRef] [Green Version]
  3. Ali, M.Z.; Javaid, A. Mechanical and rheological characterization of efficient and economical structural wood-plastic composite of wood and PVC. J. Chem. Soc. Pak. 2017, 39, 183. [Google Scholar]
  4. Hung, K.-C.; Wu, J.-H. Effect of SiO2 content on the extended creep behavior of SiO2-based wood-inorganic composites derived via the sol-gel process using the stepped isostress method. Polymers 2018, 10, 409. [Google Scholar] [CrossRef]
  5. Hafezi, S.M.; Enayati, A.; Hosseini, K.D.; Tarmian, A.; Mirshokraii, S.A. Use of amino silane coupling agent to improve physical and mechanical properties of UF-bonded wheat straw (triticum aestivum I.) poplar wood particleboard. J. For. Res 2016, 27, 427–431. [Google Scholar] [CrossRef]
  6. Sohn, J.; Cha, S. Effect of chemical modification on mechanical properties of wood-plastic composite injection-molded parts. Polymers 2018, 10, 1391. [Google Scholar] [CrossRef]
  7. Liu, J.; Declercq, N.F. Acoustic wood anomaly in transmitted diffraction field. J. Appl. Phys. 2017, 121, 114902–114921. [Google Scholar] [CrossRef]
  8. Small, A.C.; Johnston, J.H. Novel hybrid materials of magnetic nanoparticles and cellulose fibers. J. Colloid Interface Sci. 2009, 331, 122–126. [Google Scholar] [CrossRef] [PubMed]
  9. Dong, Y.; Yan, Y.; Yang, Z.; Zhang, S.; Li, J. Combined treatment for conversion of fast-growing poplar wood to magnetic wood with high dimensional stability. Wood Sci. Technol. 2016, 50, 503–517. [Google Scholar] [CrossRef]
  10. Oka, H.; Hamano, H.; Chiba, S. Experimental study on actuation functions of coating-type magnetic wood. J. Magn. Magn. Mater. 2004, 272, E1693–E1694. [Google Scholar] [CrossRef]
  11. Oka, H.; Kataoka, Y.; Osada, H.; Aruga, Y.; Izumida, F. Experimental study on electromagnetic wave absorbing control of coating-type magnetic wood using a grooving process. J. Magn. Magn. Mater. 2007, 310, e1028–e1029. [Google Scholar] [CrossRef]
  12. Oka, H.; Uchidate, S.; Sekino, N.; Namizaki, Y.; Kubota, K.; Osada, H.; Dawson, F.P.; Lavers, J.D. Electromagnetic wave absorption characteristics of half carbonized powder-type magnetic wood. IEEE Trans. Magn. 2011, 47, 3078–3080. [Google Scholar] [CrossRef]
  13. Oka, H.; Hojo, A.; Osada, H.; Namizaki, Y.; Taniuchi, H. Manufacturing methods and magnetic characteristics of magnetic wood. J. Magn. Magn. Mater. 2004, 272, 2332–2334. [Google Scholar] [CrossRef]
  14. Gan, W.; Gao, L.; Xiao, S.; Zhang, W.; Zhan, X.; Jian, L. Transparent magnetic wood composites based on immobilizing Fe3O4 nanoparticles into a delignified wood template. J. Mater. Sci. 2017, 52, 3321–3329. [Google Scholar] [CrossRef]
  15. Gan, W.; Gao, L.; Ying, L.; Zhan, X.; Jian, L. The magnetic, mechanical, thermal properties and UV resistance of CoFe2O4/SiO2-coated film on wood. J. Wood Chem. Technol. 2016, 36, 94–104. [Google Scholar] [CrossRef]
  16. Wang, H.; Yao, Q.; Wang, C.; Ma, Z.; Sun, Q.; Fan, B.; Jin, C.; Chen, Y. Hydrothermal synthesis of nanooctahedra MnFe2O4 onto the wood surface with soft magnetism, fire resistance and electromagnetic wave absorption. Nanomaterials 2017, 7, 118. [Google Scholar] [CrossRef] [PubMed]
  17. Ou, X.; He, J.; Xia, Z.; Jing, A.; Hao, J.; Xiang, Y.; He, S.; Zhao, D. Optimized microwave magnetic characteristics for patterned FeNi nanoparticle films manufactured by electric field-assisted deposition. J. Magn. Magn. Mater. 2017, 447, 61–67. [Google Scholar] [CrossRef]
  18. Butta, M.; Ripka, P.; Janosek, M.; Pribil, M. Electroplated FeNi ring cores for fluxgates with field induced radial anisotropy. J. Appl. Phys. 2015, 117, 145–149. [Google Scholar] [CrossRef]
  19. Chlenova, A.A.; Svalov, A.V.; Kurlyandskaya, G.V.; Volchkov, S.O. Magnetoimpedance of FeNi-based asymmetric sensitive elements. J. Magn. Magn. Mater. 2016, 415, 87–90. [Google Scholar] [CrossRef]
  20. Kurlyandskaya, G.V.; Chlenova, A.A.; Fernández, E.; Lodewijk, K.J. FeNi-based flat magnetoimpedance nanostructures with open magnetic flux: New topological approaches. J. Magn. Magn. Mater. 2015, 383, 220–225. [Google Scholar] [CrossRef]
  21. Zhao, H.; Zhu, Z.; Xiong, C.; Xu, X.; Lin, Q. The effect of transverse magnetic field treatment on wave-absorbing properties of FeNi alloy powders. J. Magn. Magn. Mater. 2017, 422, 402–406. [Google Scholar] [CrossRef]
  22. Li, W.; Lv, J.; Xiang, Z.; Zheng, J.; Yao, Y.; Liang, Q.; Jing, Y.; Che, S. Enhanced and broadband microwave absorption of flake-shaped Fe and FeNi composite with Ba ferrites. J. Magn. Magn. Mater. 2016, 426, 504–509. [Google Scholar] [CrossRef]
  23. Lu, X.; Liang, G.; Zhang, Y. Synthesis and characterization of magnetic FeNi3 particles obtained by hydrazine reduction in aqueous solution. Mater. Sci. Eng. B 2007, 139, 124–127. [Google Scholar] [CrossRef]
  24. Yuan, M.L.; Tao, J.H.; Yu, L.; Song, C.; Qiu, G.Z.; Li, Y.; Xu, Z.H. Synthesis and magnetic properties of Fe–Ni alloy nanoparticles obtained by hydrothermal reaction. Adv. Mater. Res 2011, 239–242, 748–753. [Google Scholar] [CrossRef]
  25. Shi, C.; Wang, L.; Wang, L. Preparation of corrosion-resistant, EMI shielding and magnetic veneer-based composite via Ni–Fe–p alloy deposition. J. Mater. Sci. Mater. Electron. 2015, 26, 7096–7103. [Google Scholar] [CrossRef]
  26. Teng, M.; Yuan, M.; Islam, S.M.; Li, H.; Ma, S.; Sun, G.; Yang, X. FeNi3 alloy nanocrystals grown on graphene: Controllable synthesis, in-depth characterization and enhanced electromagnetic performance. J. Alloys Compd. 2016, 678, 468–477. [Google Scholar] [CrossRef]
  27. Li, D.; Li, J.; Ren, B.; Li, T.; Ma, X. Synthesis and characterization of wooden magnetic activated carbon fibers with hierarchical pore structures. Polymers 2018, 10, 435. [Google Scholar] [CrossRef]
  28. Rana, R.; Langenfeld-Heyser, R.; Finkeldey, R.; Polle, A. FTIR spectroscopy, chemical and histochemical characterisation of wood and lignin of five tropical timber wood species of the family of dipterocarpaceae. Wood Sci. Technol. 2010, 44, 225–242. [Google Scholar] [CrossRef]
  29. Nguyen, V.; Hao, J.; Wang, W. Ultraviolet weathering performance of high-density polyethylene/wood-flour composites with a basalt-fiber-included shell. Polymers 2018, 10, 831. [Google Scholar] [CrossRef]
  30. Chang, H.T.; Chang, S.T. Modification of wood with isopropyl glycidyl ether and its effects on decay resistance and light stability. Bioresour. Technol. 2006, 97, 1265–1271. [Google Scholar] [CrossRef] [PubMed]
  31. Gao, H.L.; Wu, G.Y.; Guan, H.T.; Zhang, G.L. In situ preparation and magnetic properties of Fe3O4/wood composite. Mater. Technol. 2012, 27, 101–103. [Google Scholar] [CrossRef]
  32. Bheki Magagula, N.N.; Focke, W.W. Mn2al-ldh- and co2al-ldh-stearate as photodegradants for ldpe film. Polym. Degrad. Stab. 2009, 94, 947–954. [Google Scholar] [CrossRef]
  33. Alekseeva, T.; Prevot, V.; Sancelme, M.; Forano, C.; Besse-Hoggan, P. Enhancing atrazine biodegradation by pseudomonas sp. Strain ADP adsorption to layered double hydroxide bionanocomposites. J. Hazard. Mater. 2011, 191, 126–135. [Google Scholar] [CrossRef] [PubMed]
  34. Hong, R.Y.; Zhang, S.Z.; Han, Y.P.; Li, H.Z.; Ding, J.; Zheng, Y. Preparation, characterization and application of bilayer surfactant-stabilized ferrofluids. Powder Technol. 2006, 170, 1–11. [Google Scholar] [CrossRef]
  35. Hui, B.; Li, G.; Han, G.; Li, Y.; Wang, L.; Li, J. Fabrication of magnetic response composite based on wood veneers by a simple in situ synthesis method. Wood Sci. Technol. 2015, 49, 755–767. [Google Scholar] [CrossRef]
  36. Biesinger, M.C.; Payne, B.P.; Grosvenor, A.P.; Lau, L.W.M.; Gerson, A.R.; Smart, R.S.C. Resolving surface chemical states in XPS analysis of first row transition metals, oxides and hydroxides: Cr, Mn, Fe, Co and Ni. Appl. Surf. Sci. 2011, 257, 2717–2730. [Google Scholar] [CrossRef]
  37. Bokare, A.D.; Chikate, R.C.; Rode, C.V.; Paknikar, K.M. Iron-nickel bimetallic nanoparticles for reductive degradation of azo dye Orange G in aqueous solution. Appl. Catal. B 2008, 79, 270–278. [Google Scholar] [CrossRef]
  38. Kuo-cheng, H.; Ehrman, S.H. Synthesis of iron nanoparticles via chemical reduction with palladium ion seeds. Langmuir 2007, 23, 1419–1426. [Google Scholar] [CrossRef]
  39. Matsumoto, Y.; Teramoto, Y.; Nishio, Y. Preparation of thermoplastic magnetic wood via etherification and in-situ synthesis of iron oxide. J. Wood Chem. Technol. 2010, 30, 373–381. [Google Scholar] [CrossRef]
  40. Gan, W.; Gao, L.; Zhan, X.; Li, J. Hydrothermal synthesis of magnetic wood composites and improved wood properties by precipitation with CoFe2O4/hydroxyapatite. RSC Adv. 2015, 5, 45919–45927. [Google Scholar] [CrossRef]
  41. Chen, Y.P.; Wang, H.W.; Yao, Q.F.; Fan, B.T.; Wang, C.; Xiong, Y.; Jin, C.D.; Sun, Q.F. Biomimetic taro leaf-like films decorated on wood surfaces using soft lithography for superparamagnetic and superhydrophobic performance. J. Mater. Sci. 2017, 52, 7428–7438. [Google Scholar] [CrossRef]
  42. Wu, H.; Zhang, R.; Liu, X.X.; Lin, D.D.; Pan, W. Electrospinning of Fe, Co, and Ni nanofibers: Synthesis, assembly, and magnetic properties. Chem. Mater. 2007, 19, 3506–3511. [Google Scholar] [CrossRef]
  43. Bremaud, I.; Gril, J.; Thibaut, B. Anisotropy of wood vibrational properties: Dependence on grain angle and review of literature data. Wood Sci. Technol. 2011, 45, 735–754. [Google Scholar] [CrossRef]
  44. Merk, V.; Chanana, M.; Gierlinger, N.; Hirt, A.M.; Burgert, I. Hybrid wood materials with magnetic anisotropy dictated by the hierarchical cell structure. ACS Appl. Mater. Interfaces 2014, 6, 9760–9767. [Google Scholar] [CrossRef] [PubMed]
  45. Trey, S.; Olsson, R.T.; Strom, V.; Berglund, L.; Johansson, M. Controlled deposition of magnetic particles within the 3-D template of wood: Making use of the natural hierarchical structure of wood. RSC Adv. 2014, 4, 35678–35685. [Google Scholar] [CrossRef]
Polymers 11 00421 g001 550
Figure 1. Schematic of preparation for FeNi3 modified wood composites.
Figure 1. Schematic of preparation for FeNi3 modified wood composites.
Polymers 11 00421 g001
Polymers 11 00421 g002 550
Figure 2. X-ray diffraction (XRD) patterns of unmodified and modified wood. (a) Unmodified wood, (b) MW–12 wt %, (c) MW–15 wt % and (d) MW–18 wt %.
Figure 2. X-ray diffraction (XRD) patterns of unmodified and modified wood. (a) Unmodified wood, (b) MW–12 wt %, (c) MW–15 wt % and (d) MW–18 wt %.
Polymers 11 00421 g002
Polymers 11 00421 g003 550
Figure 3. Fourier transform infrared (FTIR) spectroscopy of unmodified wood and MW–18 wt %.
Figure 3. Fourier transform infrared (FTIR) spectroscopy of unmodified wood and MW–18 wt %.
Polymers 11 00421 g003
Polymers 11 00421 g004 550
Figure 4. Scanning electron microscopy (SEM) images of unmodified wood and MW–18 wt %. (a) Unmodified wood (2000×), (b) modified wood (2000×), (c) FeNi3 nanoparticles (100,000×), (d) FeNi3 nanoparticles (1,000,000×).
Figure 4. Scanning electron microscopy (SEM) images of unmodified wood and MW–18 wt %. (a) Unmodified wood (2000×), (b) modified wood (2000×), (c) FeNi3 nanoparticles (100,000×), (d) FeNi3 nanoparticles (1,000,000×).
Polymers 11 00421 g004
Polymers 11 00421 g005 550
Figure 5. Energy-dispersive X-ray (EDX) spectrum of MW–18 wt %.
Figure 5. Energy-dispersive X-ray (EDX) spectrum of MW–18 wt %.
Polymers 11 00421 g005
Polymers 11 00421 g006 550
Figure 6. X-ray photoelectron spectroscopy (XPS) spectra of unmodified wood and MW–18 wt %. (a) Unmodified wood, (b) MW–18 wt %, (c) XPS spectrum of Fe 2p and (d) XPS spectrum of Ni 2p.
Figure 6. X-ray photoelectron spectroscopy (XPS) spectra of unmodified wood and MW–18 wt %. (a) Unmodified wood, (b) MW–18 wt %, (c) XPS spectrum of Fe 2p and (d) XPS spectrum of Ni 2p.
Polymers 11 00421 g006
Polymers 11 00421 g007 550
Figure 7. Magnetization curves of modified wood composites. (a) MW–12 wt %, MW–15 wt % and MW–18 wt %. (b) MW–18 wt % at parallel and vertical direction.
Figure 7. Magnetization curves of modified wood composites. (a) MW–12 wt %, MW–15 wt % and MW–18 wt %. (b) MW–18 wt % at parallel and vertical direction.
Polymers 11 00421 g007
Polymers 11 00421 g008 550
Figure 8. Digital images of the modified wood with an excellent magnetic property. (a) Magnetic wood can be firmly attracted by permanent magnet. (b) The specimen floating on the surface of the water. (c) The specimen can be attracted to the bottom of the cup by an external magnet.
Figure 8. Digital images of the modified wood with an excellent magnetic property. (a) Magnetic wood can be firmly attracted by permanent magnet. (b) The specimen floating on the surface of the water. (c) The specimen can be attracted to the bottom of the cup by an external magnet.
Polymers 11 00421 g008

Share and Cite

MDPI and ACS Style

Wang, L.; Li, N.; Zhao, T.; Li, B.; Ji, Y. Magnetic Properties of FeNi3 Nanoparticle Modified Pinus radiata Wood Nanocomposites. Polymers 2019, 11, 421. https://doi.org/10.3390/polym11030421

AMA Style

Wang L, Li N, Zhao T, Li B, Ji Y. Magnetic Properties of FeNi3 Nanoparticle Modified Pinus radiata Wood Nanocomposites. Polymers. 2019; 11(3):421. https://doi.org/10.3390/polym11030421

Chicago/Turabian Style

Wang, LiLi, Na Li, Tiqi Zhao, Bin Li, and Yali Ji. 2019. "Magnetic Properties of FeNi3 Nanoparticle Modified Pinus radiata Wood Nanocomposites" Polymers 11, no. 3: 421. https://doi.org/10.3390/polym11030421

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop