Microstructural Engineering of Magnetic Wood for Enhanced Magnetothermal Conversion

Abstract

The increasing energy crisis demands sustainable functional materials. Wood, with its natural three-dimensional porous structure, offers an ideal renewable template. This study demonstrates that microstructural engineering of wood is a decisive strategy for enhancing magnetothermal conversion. Using eucalyptus wood, we precisely tailored its pore architecture via delignification and synthesized Fe₃O₄ nanoparticles in situ through coprecipitation. We systematically investigated the effects of delignification and precursor immersion time (24, 48, 72 h) on the loading, distribution, and magnetothermal performance of the composites. Delignification drastically increased wood porosity, raising the Fe₃O₄ loading capacity from ~5–6% (in non-delignified wood) to over 14%. Immersion time critically influenced nanoparticle distribution: 48 h achieved optimal deep penetration and uniformity, whereas extended time (72 h) induced minor local agglomeration. The optimized composite (MDW-48) achieved an equilibrium temperature of 51.2 °C under a low alternating magnetic field (0.06 mT, 35 kHz), corresponding to a temperature rise (ΔT) > 24 °C and a Specific Loss Power (SLP) of 1.31W·g⁻¹. This performance surpasses that of the 24 h sample (47 °C, SLP = 1.16 W·g⁻¹) and rivals other bio-based magnetic systems. This work establishes a clear microstructure–property relationship: delignification enables high loading, while controlled impregnation tunes distribution uniformity, both directly governing magnetothermal efficiency. Our findings highlight delignified magnetic wood as a robust, sustainable platform for efficient low-field magnetothermal conversion, with promising potential in low-carbon thermal management.

1. Introduction

The increasingly severe global energy crisis is driving an urgent search for sustainable materials derived from renewable resources. Among these, wood—a naturally occurring three-dimensional scaffold that is abundant, lightweight, and possesses excellent mechanical properties—has demonstrated immense potential [1]. By integrating inorganic nanomaterials into its unique multi-scale pore structure, functionalization research on wood has opened new avenues for developing advanced composite materials [2]. Specifically, the incorporation of magnetic elements—such as Fe, O, NdFeB, and others—has given rise to wood-based magnetic composites, elevating natural timber into advanced functional materials suitable for modern applications.

Magnetic nanoparticles have garnered significant attention in recent years due to their unique magnetocaloric effect (also known as the magnetocaloric phenomenon) [3]. First proposed by J. C. Maxwell in the 19th century, this effect describes the significant temperature change in materials caused by magnetic moment rearrangement under an applied alternating magnetic field [4]. Based on this principle, magnetic nanoparticles enable efficient conversion of magnetic energy into thermal energy [5], demonstrating application value in biomedicine [6,7,8,9,10], magnetic refrigeration [11,12,13,14,15], and smart electronic devices [16,17].

However, the realization of these applications heavily relies on the development of high-performance magnetocaloric materials. Magnetic nanoparticles still face multiple challenges in practical applications, including biocompatibility, colloidal stability, agglomeration, and sustainability [18,19,20,21,22]. To overcome these limitations, an effective strategy is to composite them with functional matrices to construct structurally stable, functionally integrated composite systems [23]. Researchers have attempted to composite magnetic components like Fe₃O₄ and Co with carbon-based materials (e.g., expanded graphite, carbon nanotubes) [24,25,26] and phase-change matrices (e.g., SA, PEG) [27,28,29], successfully developing multifunctional composites with high-efficiency photothermal/magnetothermal synergistic conversion capabilities and excellent cycling stability. These efforts validate the feasibility of the composite strategy for enhancing the comprehensive performance of magnetothermal materials.

Among various matrix options, wood offers an ideal carrier for efficient magnetothermal conversion and thermal energy storage due to its inherent three-dimensional interconnected porous framework, excellent mechanical properties, renewability, and tunable interfacial characteristics [30]. Research indicates that incorporating magnetic nanoparticles like Fe₃O₄ with phase-change media such as polyethylene glycol (PEG) and tetradecanol into porous wood-based substrates—including delignified wood and carbonized wood powder—enables the construction of multifunctional composite systems. These materials exhibit high phase-change enthalpy, outstanding cycling stability, and significant magnetothermal temperature rise [31,32]. They demonstrate broad application prospects in building energy efficiency, human comfort regulation, and sustainable thermal energy management [33,34].

In summary, wood-based magnetic composites ingeniously integrate the structural advantages of natural wood with the functional properties of magnetic nanoparticles, opening new avenues for developing sustainable, high-performance magnetocaloric devices. However, systematic research on the magnetothermal conversion of such materials remains relatively scarce. In particular, the structure–property relationship between their magnetothermal conversion performance and the microstructure of wood, the loading amount of magnetic nanoparticles, and their distribution morphology remains unclear. This significantly limits further optimization of their performance and the precise exploration of application scenarios.

Therefore, by elucidating the fundamental structure–property relationship between wood microstructure, magnetic nanoparticle distribution, and magnetothermal conversion efficiency, the microstructurally engineered composite developed in this study presents a sustainable and high-performance material platform. This delignified wood-based composite not only offers a scalable and eco-friendly fabrication pathway but also demonstrates significant potential for industrial applications—such as in low-carbon building materials for interior heating, localized thermal therapy devices in biomedicine, or energy-management components in smart furniture and packaging—due to its integrated biocompatibility, structural robustness, and efficient energy conversion. Thus, this work provides both valuable scientific insights for the field of magnetic composite chemistry and engineering and a practical strategy to address the dual demands of efficiency and sustainability in next-generation thermal management systems.

Figure 1 shows the experimental flowchart. Addressing this research gap, this study aims to systematically investigate magnetothermal conversion performance of wood-based magnetic composites, focusing on revealing the structure–property relationship governing their magnetothermal conversion efficiency. To achieve this, we employed a simple in situ synthesis method to generate Fe₃O₄ nanoparticles within eucalyptus wood samples. The porous structure of the wood template was precisely controlled through a delignification process. We thoroughly investigated the effects of impregnation time in the precursor solution (24, 48, and 72 h) on the loading capacity and distribution morphology of the magnetic phase. Additionally, the role of subsequent densification treatment on the structure and properties of the composite materials was evaluated. The magnetothermal conversion capabilities of all prepared composites were quantitatively assessed using a custom-built alternating magnetic field apparatus.

2. Experimental Section

2.1. Material

This experiment utilized eucalyptus wood with dimensions of 40 mm × 50 mm × 2 mm (length × width × height) as the initial material, and the eucalyptus wood was provided by Zhejiang Shenghua Yunfeng Greeneo Co., Ltd. (Huzhou, China). The eucalyptus blocks were placed in distilled water for 30 min of ultrasonic cleaning and then dried under vacuum at 80 °C for 48 h. Experimental reagents Na₂SO₃, NaOH, FeSO₄·7H₂O, and FeCl₃·6H₂O were purchased from Shanghai Aladdin Biochemical Technology Co., Ltd. (Shanghai, China). Deionized water was prepared in the laboratory for experimental use.

2.2. Preparation of Delgified Wood

De-lignify the eucalyptus wood. Weigh 15 g of Na₂SO₃ and dissolve it in 150 mL of deionized water to form a 10% Na₂SO₃ solution. Weigh 0.6 g of NaOH and dissolve it in 150 mL of deionized water to form a 0.1 M NaOH solution. Place the eucalyptus wood sample into the reaction vessel. Add 150 mL of the 10% Na₂SO₃ solution to the reaction vessel, ensuring the sample is fully submerged. Add 150 mL of the 0.1 M NaOH solution to achieve a 1:1 volume ratio with the Na₂SO₃ solution. Heat the reaction vessel to 90 °C and maintain this temperature while stirring continuously for 4–6 h. Ensure the wood sample remains fully submerged in the solution throughout. After processing, remove the wood sample from the solution and rinse thoroughly with copious amounts of deionized water to remove residual chemicals. Place the wood samples in a well-ventilated area to air-dry naturally, or dry them in an oven at a low temperature (<60 °C) until completely dry. This yields delignified eucalyptus samples (DW). A separate portion of undelignified eucalyptus samples was washed and dried. This ensures that the eucalyptus samples are thoroughly delignified and suitable for subsequent magnetic composite preparation.

2.3. Preparation of Wood-Based Magnetic Composites

Prepare the FeSO₄-FeCl₃ precursor solution. Prepare 100 mL of a mixed solution containing 0.5 mol/L FeSO₄·7H₂O and 0.5 mol/L FeCl₃·6H₂O in a 2:1 ratio. Stir the solution using a magnetic stirrer to ensure complete dissolution. Immerse delignified and undelignified eucalyptus wood samples into the solution. After thorough wetting, impregnate them at room temperature and atmospheric pressure for 24 h, 48 h, and 72 h, respectively. After immersion in the precursor solution, thoroughly rinse the samples with deionized water. Then, hydrolyze them in a 1 mol/L NaOH solution for 24 h. Finally, rinse thoroughly with deionized water until the system is neutralized. Dry the samples in a 50 °C oven to obtain magnetic Fe₃O₄ wood-based composites (MDW and MW). As shown in

Table 1. Treatment conditions of different samples and Fe₃O₄ loading rates.

Sample	Delignification	Immersion Time in the Precursor Solution	Wn (g)	Wm (g)	Rm (%)
W	No	/	3.37	3.37	0
DW	Yes	/	2.44	2.44	0
MW-24	No	24 h	3.31	3.47	4.7
MW-48	No	48 h	3.26	3.44	5.1
MW-72	No	72 h	3.35	3.58	6.5
MDW-24	Yes	24 h	2.42	2.63	8.0
MDW-48	Yes	48 h	2.41	2.83	14.8
MDW-72	Yes	72 h	2.51	2.96	15.2

below, eight sets of samples were prepared under different conditions based on lignin removal status and precursor solution immersion time.

Among them, the loading rate of Fe₃O₄ nanoparticles on wood is calculated using the following formula:

$${\mathrm{R}}_{\mathrm{m}}(\%)=({\mathrm{W}}_{\mathrm{m}}-{\mathrm{W}}_{\mathrm{n}})/{\mathrm{W}}_{\mathrm{m}}\times 100$$

R_m is the loading rate of Fe₃O₄ nanoparticles on the wood, W_m is the weight of the magnetic wood, and W_n refers to the weight of the wood sample before treatment. Treatment conditions of different samples and Fe₃O₄ loading rates are shown in Table 1 and Figure 2.

2.4. Compaction Treatment

The compaction (hot-pressing) treatment is a common process in advanced wood manufacturing, known to significantly enhance the density and mechanical properties of wood-based materials [35,36,37,38]. Therefore, in this study, a standard hot-pressing treatment was applied as the integral final step in fabricating all wood-based magnetic composites, aiming to produce structurally robust samples suitable for practical applications.

Figure 3 shows a schematic diagram of the preparation process: Panel I presents the morphology of natural eucalyptus wood (W), delignified eucalyptus wood (DW), and magnetic eucalyptus wood (MDW) after impregnation with the precursor solution; Panel II illustrates the preparation of the precursor solution and the impregnation process; Panel III highlights a critical divergence observed after the compaction treatment among different sample groups.

However, a clear distinction was observed upon compaction: samples from the non-delignified magnetic wood group (MW) exhibited severe structural failure upon compaction. Specifically, the Fe₃O₄ nanoparticles, which were predominantly surface-adhered due to the impeded penetration caused by the dense lignin network, were extensively extruded under the combined heat and pressure. This resulted in visible material overflow and a highly inhomogeneous distribution of the magnetic phase. Consequently, the compacted MW samples were deemed unsuitable for reliable and representative magnetothermal performance evaluation and were excluded from the subsequent quantitative analysis.

This stark contrast powerfully underscores the pivotal role of delignification. The process creates an open, permeable cellulose framework that not only facilitates deep and uniform loading of Fe₃O₄ nanoparticles but also confers sufficient structural integrity to withstand standard densification processes without functional degradation. The following sections, therefore, focus on the characterization and performance evaluation of the delignified magnetic wood composites (MDW series), which successfully integrate enhanced magnetic functionality with the structural benefits of compaction.

2.5. Characterization

Using a high-resolution scanning electron microscope (SEM, Zeiss Sigma 300, Oberkochen, Germany), observe the surface and cross-sectional structures of different samples. Pay particular attention to the distribution of magnetic nanoparticles within the wood fiber and pore structures, evaluating particle uniformity and fixation. Employ X-ray diffraction (XRD, Ultima IV combined multifunctional horizontal X-ray diffractometer, Tokyo, Japan) technology to determine the crystal structure of magnetic nanoparticles in various samples.

2.6. Magnetothermal Conversion Experiment

A homemade magnetothermic device was constructed using a 2 mm copper wire coil and a resonant PLC circuit to generate a constant alternating magnetic field for measuring the magnetothermal conversion performance in magnetic wood. During the experiment, wood samples were excited under a magnetic field frequency of 35 kHz, with a magnetic field strength of 0.06 mT, a coil diameter of 35 mm, a voltage of 12 V, and a current of 5 A. An infrared thermal imager (FLIR, Jasco 4600 instrument, Tokyo, Japan) was employed to record real-time changes in the wood surface temperature. To ensure the reliability and reproducibility of the results, each magnetothermal test was performed twice on independent samples from the same batch, with an interval of 5 days between measurements. The reported temperature profiles and derived parameters are the averages of these two highly concordant runs.

The magnetothermal conversion efficiency was quantitatively evaluated by calculating the Specific Loss Power (SLP).

$$SLP={\displaystyle \frac{C·m}{m_{np}}}\times {\displaystyle \frac{\mathsf{\Delta }T}{\mathsf{\Delta }t}}$$

C: The specific heat capacity of the wood-based sample. A value of 1.7 J·g⁻¹·°C⁻¹, characteristic of dry wood, was adopted for the composite [32].

m: The mass of the wood sample.

m_np: The total mass of the magnetic nanoparticles loaded on the wood (g).

$\mathsf{\Delta }T$/$\mathsf{\Delta }t$: The initial linear heating rate was determined from the slope of the linear regression fit applied to the temperature–time data within a stable linear heating period (30–120 s after magnetic field activation). This period was selected to avoid any initial transient response and ensure excellent linearity (R² > 0.99 for all samples).

3. Results

3.1. Morphological and Structural Characteristics of Magnetic Wood

Figure 4 displays structural characterization images of W, DW, and MDW samples at 24–72 h. As shown in Figure 4a, the SEM image of untreated natural eucalyptus wood (W) clearly reveals the wood’s porous structure. The cell walls and middle lamellae of the wood cells appear largely intact, with most vessel walls tightly integrated.

As shown in Figure 4b, the SEM image depicts the delignified eucalyptus sample (DW). Comparing the photographs reveals the appearance of numerous gaps and a distinctly roughened, delaminated texture on the radial cross-section. This occurs because wood cell walls are primarily composed of cellulose, hemicellulose, and lignin. Delignification disrupts the structural stability of lignin, causing it to dissociate and dissolve from the cellulose and hemicellulose network [1]. Consequently, the porosity of the wood structure increases significantly, pore sizes enlarge, cell cavities expand, and some cell walls collapse or fracture, resulting in uneven grooves and microfibril bundles on the surface. This provides additional anchoring sites and diffusion pathways for subsequent Fe₃O₄ nanoparticle loading.

As shown in Figure 4c–e, SEM images of MDW-24, MDW-48, and MDW-72 after in situ coprecipitation reveal that Fe₃O₄ adsorption within the MDW series markedly increases with prolonged impregnation time (24 h → 72 h). This occurs because, within a short timeframe (24 h), ion diffusion dominates, leading particles to preferentially load onto surfaces and macropores. As time extends (48 h), deeper pores are progressively filled, and particle size tends toward uniformity. However, excessive prolongation may cause particles to clog pores (local agglomeration observed in MDW-72, Figure 4e). In summary, delignification treatment significantly enhances Fe₃O₄ nanoparticle loading efficiency and distribution uniformity by optimizing wood microstructure and surface chemistry, while impregnation time further optimizes loading capacity by regulating ion penetration depth.

3.2. Wood-Crystal Structure and Chemical Composition

The crystal structure of the experimental samples was tested using XRD. Figure 5 shows the XRD patterns of W, DW, and MDW-24~72. The characteristic peaks at 15.6° and 22.4° in the W pattern correspond to the (100) and (002) crystallographic planes of cellulose. The DW pattern matches W’s characteristic peaks, confirming that delignification does not alter the crystallographic structure of the eucalyptus sample. The XRD pattern of Fe₃O₄ nanoparticles exhibits characteristic peaks at 30.1°, 35.4°, 43.1°, 53.4°, 56.9°, and 62.5°, corresponding to the (220), (311), (400), (422), (511), and (440) crystal planes, consistent with the pdf standard card for magnetite (JCPDS NO.19-0629).

The characteristic peaks in the MDW24~72 h pattern curve, in addition to those corresponding to cellulose crystal planes, also exhibit six additional peaks matching the Fe₃O₄ nanoparticle pattern, confirming the successful synthesis of Fe₃O₄ magnetic nanoparticles in the MDW-24~72 samples. Furthermore, MDW-48 and MDW-72 exhibit more pronounced characteristic peaks compared to MDW-24, indicating that the Fe₃O₄ loading in MDW-48 and MDW-72 is greater than that in MDW-24.

The average crystallite size of the Fe₃O₄ nanoparticles within the magnetic wood composites was estimated from X-ray diffraction (XRD) data. Using the full width at half maximum (FWHM) of the most intense (311) diffraction peak of Fe₃O₄ in the XRD pattern, the Scherrer equation is presented as follows:

$$D={\displaystyle \frac{K\lambda }{\beta cos\theta }}$$

Here, D represents the average crystallite diameter, K is the shape factor (taken as 0.9), λ is the X-ray wavelength (0.15406 nm), β is the FWHM of the diffraction peak (in radians), and θ is the Bragg diffraction angle. The calculated average crystallite size of the Fe₃O₄ nanoparticles is approximately 12.8 nm.

3.3. Magnetic Properties of the Composites

To quantitatively evaluate the distribution of the magnetic phase and corroborate the successful loading of Fe₃O₄ nanoparticles, the magnetic properties of representative samples were characterized using a Vibrating Sample Magnetometer (VSM) at room temperature.

As shown in Figure 6, all MDW samples exhibit typical ferrimagnetic hysteresis loops, whereas native wood (W) and delignified wood (DW) show only negligible diamagnetic responses, confirming that the magnetization originates solely from the incorporated Fe₃O₄ phase. Furthermore, all MDW samples display low coercivity and negligible remanence, indicating that the embedded Fe₃O₄ nanoparticles exhibit near-superparamagnetic behavior at room temperature—a property favorable for efficient magnetothermal conversion via Néel relaxation.

A clear trend is observed in the saturation magnetization (Ms) values: MDW-48 exhibits the highest Ms (12.8 emu/g), followed by MDW-72 (11.9 emu/g) and MDW-24 (5.2 emu/g). This progression aligns closely with the gravimetrically determined Fe₃O₄ loading rates (Rm, Table 1). Such a strong positive correlation provides direct magnetic evidence that the Fe₃O₄ nanoparticles are distributed throughout the bulk volume of the wood matrix rather than merely deposited on the surface. The highest Ms of MDW-48 corresponds to its optimal nanoparticle loading and uniform distribution, as observed in SEM images (Figure 4d). The slightly lower Ms of MDW-72 is consistent with the localized agglomeration noted in SEM (Figure 4e), which may reduce the effective magnetic moment per unit mass due to inter-particle interactions.

In summary, the VSM results not only confirm the successful integration of magnetic nanoparticles but also establish a direct microstructure–magnetic property relationship, where improved nanoparticle loading and distribution uniformity lead to enhanced magnetic response—a key factor underpinning the magnetothermal performance discussed in the following section.

3.4. Magnetothermal Conversion Properties of Wood

3.4.1. Magnetothermal Performance and Macroscopic Heating Behavior

The author’s self-made alternating magnetic field magnetocaloric testing device is used to determine the magnetothermal conversion performance of the sample [34]. The alternating magnetic field works at a frequency of 35 kHz, with a magnetic flux density of 0.06 mT and a current of 5 A. The experimentally prepared wood-based magnetic materials are placed in the device. The surface temperature changes in the wood-based magnetic materials are measured using an infrared thermal imager, thereby calculating their magnetothermal conversion efficiency. To assess the reproducibility and stability of the measurement, each sample underwent two independent tests with a 5-day interval between runs. The data presented in Figure 7 and

Table 2. Temperature changes in the wood-based magnetic samples DW, MDW-24, MDW-48, and MDW-72.

Duration/Min	W/°C	DW/°C	MDW-24/°C	MDW-48/°C	MDW-72/°C
0	26.6	26.3	27.2	26.9	25.9
0.50	27.4	26.6	29.1	28.4	28.1
1.00	26.9	27.6	30.2	30.4	32.7
1.50	27.5	26.8	32.1	34.9	35.4
2.00	26.3	26.7	33.9	38.3	38.5
2.50	26.4	27.9	36.8	40.6	41.5
3.00	26.9	27.2	37.4	42.9	41.8
3.50	27.6	27.8	39	45.3	45.5
4.00	27.1	27.9	42.8	47.7	47
4.50	26.7	27.5	44.3	48.1	50.5
5.00	27.3	27.3	45.6	50.5	50.9
5.50	27.8	27.8	47.3	51.5	51.1
6.00	26.4	26.9	46.4	50.8	51.7
6.50	27.6	27.8	46.3	51.9	51.0
7.00	27.1	27.2	47.1	52.1	51.6
7.50	27.4	27.5	46.6	51.4	52.1
8.00	26.7	27.7	47.3	51.5	51.9

represent the average of these two highly consistent measurements. Figure 7 and Table 2 show the temperature change in the wood-based magnetic samples DW and MDW-24~72 after being subjected to an alternating magnetic field for 8 min.

The surface temperature of sample W and DW remained consistently between 26 °C and 27 °C over time. This demonstrates that untreated wood, not impregnated with the reaction solution, exhibits no magnetothermal conversion performance under a 35 kHz alternating magnetic field.

Samples MDW-24, MDW-48, and MDW-72 exhibit a rapid temperature rise over time, stabilizing at approximately 5 min and 30 s. This demonstrates that wood-based magnetic materials immersed in the reaction solution exhibit strong magnetothermal conversion performance under a 35kHz alternating magnetic field.

The average peak temperature for sample MDW-24 was 47 °C, while samples MDW-48 and MDW-72 reached an average peak temperature of approximately 51.2 °C. This demonstrates that the magnetothermal conversion performance of wood-based magnetic materials correlates with the immersion duration in the reaction solution during testing. Longer immersion periods increase the loading rate of Fe₃O₄ nanoparticles within the material, thereby enhancing its magnetothermal conversion performance. Furthermore, after 48 h of immersion, the Fe₃O₄ nanoparticle loading rate in the wood-based magnetic material essentially reaches saturation, leading to a stable magnetothermal conversion performance. The high reproducibility of the heating profiles between the two independent tests confirms the robustness of the experimental data and indicates the short-term stability of the Fe₃O₄ nanoparticles within the wood matrix. No performance degradation was observed between the tests, suggesting that the in situ synthesized nanoparticles are effectively anchored in the delignified cellulose framework.

3.4.2. Quantitative Analysis of Magnetothermal Conversion Efficiency

To enable direct comparison with other magnetothermal material systems, the Specific Loss Power (SLP) was calculated for the MDW series. The key parameters and results are summarized in

Table 3. The SLP values of the magnetic wood composites.

Sample	Rm (%)	Mnp (g)	ΔT/Δt (°C·s−1)	SLP (W·g−1)
MDW-24	8.00	0.21	0.05	1.16
MDW-48	14.80	0.42	0.11	1.31
MDW-72	15.20	0.45	0.11	1.26

.

As shown in Table 3, MDW-48 exhibits the highest SLP value (1.31 W·g⁻¹), which correlates directly with its highest Fe₃O₄ loading (14.8%) and the most uniform nanoparticle distribution observed in SEM images (Figure 4d). A high and uniform loading ensures maximum utilization of nanoparticles for efficient magnetothermal conversion under the alternating magnetic field. The SLP of MDW-72 (1.26 W·g⁻¹) is slightly lower, consistent with the incipient local agglomeration of nanoparticles (Figure 4e), which may reduce effective magnetic relaxation losses. MDW-24 shows the lowest SLP (1.16 W·g⁻¹), in agreement with its lowest loading rate (8.0%) and shallower particle penetration.

This quantitative SLP trend—MDW-48 ≈ MDW-72 > MDW-24—is fully consistent with the observed macroscopic equilibrium temperatures (Figure 6) and the microstructural characterization. It provides conclusive evidence, from the perspective of energy conversion rate, that engineering the wood template through delignification to create an open porous structure, combined with an optimal 48 h impregnation duration, is the key to achieving the highest magnetothermal conversion performance.

4. Conclusions

This work successfully demonstrates a microstructure-driven strategy for transforming natural wood into an efficient magnetothermal material. The key lies in the sequential engineering of its porous architecture: delignification opens the internal wood network, while controlled impregnation time (48 h) ensures optimal Fe₃O₄ nanoparticle loading and distribution. This two-step process results in composites where the magnetic phase is uniformly embedded within the wood bulk, as confirmed by cross-sectional SEM, VSM, and magnetothermal analysis. The established structure–property relationship is clear: samples with higher and more homogeneous nanoparticle loading (notably MDW-48) exhibit stronger magnetic response and superior magnetothermal conversion efficiency under low-field conditions. The excellent reproducibility of the heating profiles further attests to the stability of the composite. Beyond presenting a high-performance material, this study provides a generalizable and sustainable fabrication route that leverages the innate structure of wood. The proposed magnetic wood composite thus emerges as a promising, eco-friendly platform for thermal management applications, showcasing how green process engineering can unlock advanced functionalities in renewable biomass.