ZrC/C nanofibers were synthesized via a carbothermal reduction process. A carbon source solution was first prepared by dissolving sucrose ( C₁₂H₂₂O₁₁, Adamas) and polyvinylpyrrolidone (as a spinning aid) in N,N-dimethylformamide under stirring at 80^∘C for 2 h. Separately, a zirconium precursor solution was formulated by mixing Zirconium (IV) n-propoxide with anhydrous ethanol and acetylacetone (chelating agent) in a volume ratio of 4:3:1, followed by stirring at room temperature for 2 h. The two solutions were then combined and stirred for 8 h at room temperature to obtain a homogeneous spinnable sol. The precursor nanofibers were produced by electrospinning of the resultant sol, which were subsequently stabilized at 350^∘C and then carbonized at 1500^∘C to yield ZrC/C nanofibers, denoted as ZC. The reaction process within ZC nanofibers is clearly depicted in Fig. S4.

The transformation of ZrC/C nanofibers into ZrO₂/C nanofibers was achieved through an in-situ oxidation process. To investigate the effect of oxidation temperature, ZC nanofibers were oxidized at 500^∘C,600^∘C and 700^∘C for 5 minutes, yielding samples designated as ZCO-500-5, ZCO-600-5 and ZCO-700-5, respectively. To further examine the influence of oxidation time, isothermal treatments were conducted at 600^∘C for 3,5 and 10 minutes, with the resulting nanofibers labeled accordingly as ZCO-600-3, ZCO-600-5 and ZCO-600-10 (Fig. S5). The schematic diagram of the preparation process of ZC and ZCO nanofibers, as well as the macroscopic morphology of the prepared nanofibers, are shown in Fig.1.

Simultaneous thermal analysis (TG-DSC, NETZSCH STA 449F3) was conducted in air atmosphere with the temperature raised from room temperature to 1100^∘C at a heating rate of 7 ^∘C/min. The crystal structures of the ZC and ZCO nanofibers were analyzed by X-ray diffraction (XRD, D8 Advance, Bruker, Germany). The surface chemical composition of the nanofibers was characterized using X-ray photoelectron spectroscopy (XPS, Thermo Scientific K-Alpha). Microstructural and morphological features were examined in a scanning electron microscope (SEM, JSM-IT800, JEOL, Japan). Raman spectroscopy (HORIBA LabRam HR Evolution, Japan) was employed to evaluate the structural order and defects of the carbon phase within the surface region of the nanofibers. To obtain detailed crystallographic information, focused ion beam (FIB, Thermo Scientific Scios 2) was used to prepare lamellae from fiber fractures, which were then analyzed by transmission electron microscopy (TEM, JEM-F200, JEOL, Japan), high-resolution TEM (HRTEM) and aberration-corrected TEM (ACTEM, Thermo Scientific Spectra Ultra). Moreover, the electromagnetic parameters in the frequency range of 2.0-18.0GHz were measured using a vector network analyzer (Agilent N5244A, Keysight Technologies, Inc.). For these measurements, the fiber samples were homogeneously mixed with wax at a concentration of 5wt.% and pressed into toroidal-shaped specimens with an outer diameter of 7.00 mm and an inner diameter of 3.04 mm.

The XRD pattern of the ZC nanofibers is presented in Fig. 2a, which clearly reveals the presence of a cubic ZrC phase (PDF#97-061-9153). To further investigate the chemical composition and elemental valence states, XPS analysis was conducted on the ZC nanofibers. Fig. S1 shows the XPS survey scan of ZC nanofibers. The C 1s spectrum (Fig. 2d) could be deconvoluted into four characteristic peaks, corresponding to C-C,C-O,C=O and Zr-C bonds, respectively [11-12]. The O1s spectrum (Fig. 2e) indicates the presence of Zr-O (530.5 eV), O-C (532.0 eV) and O=C(532.9eV) bonds, which can be assigned to lattice oxygen, surface oxygen vacancies and adsorbed oxygen species, respectively [13-14]. Furthermore, the XPS spectrum of Zr3d (Fig. 2f) confirms that the primary chemical bonds on the surface consist of Zr-C and Zr-O bonds. Fig. 2c shows the Raman spectra of both ZC and ZCO nanofibers. Two distinct peaks are observed near 1590 cm^-1 (G-band) and 1340 cm^-1 (D-band), which are attributed to the highly ordered graphitic lattice and structural defects in carbon materials, respectively. The I_D/I_G intensity ratio is commonly used to evaluate the graphitization degree of carbonaceous materials [15]. The ZC nanofibers exhibit an I_D/I_G ratio of 1.13, which indicates that the fibrous structure consists of amorphous carbon. [16]. To achieve the controlled transformation of ZC nanofibers into ZCO nanofibers, a thorough understanding of the oxidation mechanism is essential. Based on the TG-DSC curves shown in Fig. 2b, the oxidation process of the ZC nanofibers can be divided into four distinct stages [17]. The first stage ( 25-270^∘C ) exhibits a mass loss of approximately 1wt\%, attributed to the evaporation of adsorbed water from the fiber surface. In the second stage (270-433^∘C ), a significant mass gain of 19.8% is observed, accompanied by a distinct exothermic peak at 380^∘C on the DSC curve. This temperature corresponds to the maximum mass gain rate and indicates the occurrence of an exothermic reaction involving the oxidation of ZrC to ZrO₂. The third stage (433594^∘C) shows a remarkable mass loss of 40.8%, with an exothermic peak at 541^∘C on the DSC curve coinciding with the sharp mass decrease, resulting from the oxidation of the amorphous carbon matrix. During the fourth stage (594-1100  ^∘C ), the gradual mass loss can be primarily attributed to the slow yet continuous oxidation of the carbon matrix. The relatively low oxidation rate is likely due to the partial protective effect conferred by the ZrO₂. To achieve conversion of ZrC to ZrO₂ while preventing excessive oxidation of the carbon matrix, oxidation temperatures of 500^∘C,600^∘C and 700^∘C were selected for subsequent experiments.

The phase compositions of the ZCO nanofibers after oxidation at different temperatures are shown in Fig. 2a. In the ZCO-500-5 sample, the intensity of the ZrC diffraction peaks exhibits a slight decrease compared to the pristine ZC nanofibers. As the oxidation temperature increases, the ZCO-600-5 sample is predominantly characterized by an amorphous ZrO₂ phase, with the ZrC peaks significantly weakened and obscured due to a substantial reduction in crystalline content. The ZCO-700-5 sample exhibited distinct and sharp diffraction peaks, which are indicative of the crystallization tendency of ZrO₂ at elevated temperatures. Considering the potentially complex structure of ZCO-600-5, which may comprise both amorphous and nanocrystalline ZrO₂, gradient oxidation experiments with varying durations were conducted at 600^∘C to further elucidate its phase evolution. The reduction in intensity of the ZrC diffraction peaks is clearly observed in the ZCO-600-3 sample, whereas well-defined crystalline diffraction peaks corresponding to ZrO₂ emerge in the ZCO-600-10 sample. Furthermore, the nearly identical I_D/I_G ratios observed for the ZCO nanofibers (Fig. 2c) indicate that the low-temperature oxidation process exerts minimal influence on the graphitization degree of the carbon matrix. Crystallinity and amorphous content significantly influence the EMW absorption performance of the material. Higher crystallinity tends to enhance the reflection and scattering of EMWs. In contrast, a higher amorphous content generally contributes to improved impedance matching, reducing reflection at the material-air interface and thereby enhancing absorption [18]. Therefore, the ZCO-600-5 sample, with its moderate crystallinity, is considered more conducive to achieving efficient EMW absorption and has been selected as the optimal sample for further investigation in this study.

Fig. 3 presents SEM images of the pristine ZC nanofibers and the ZCO nanofibers obtained under different oxidation conditions. The ZC nanofibers exhibit a smooth surface and an average diameter of approximately 550 nm (Fig. 3a). As the oxidation proceeds, the ZrC phase gradually transforms into ZrO₂, accompanied by the formation of micro-protrusions on the nanofibers surface. Meanwhile, the carbon matrix is progressively consumed through oxidation, leading to a gradual reduction in fiber diameter (Fig. S2). The oxidation degree plays a decisive role in determining the final microstructure. For instance, ZCO-600-10 nanofibers (Fig. 3e) experienced excessive oxidation, which resulted in substantial depletion of the carbon matrix. As a result, the fiber diameter was significantly reduced to 470 nm, and the surface became entirely covered with coarse ZrO₂ particles. This structural evolution would disrupt the original conductive network, thereby adversely affecting the microwave absorption performance. Among all the samples, ZCO-600-5 nanofibers (Fig. 3d) exhibits the most desirable morphological characteristics. Its surface displays uniformly distributed and moderately sized micro-protrusions (Fig. S3), which are beneficial for enhancing multiple reflections and scattering of EMWs. Therefore, the ZCO-600-5 sample, which exhibits a combination of moderate crystallinity and favorable morphology, is regarded as the most suitable candidate for efficient EMW absorption and has been chosen for further investigation in this study.

The microstructure of the ZC nanofibers was thoroughly characterized using HRTEM. The high-resolution image in Fig. 4a and the corresponding EDS results in Fig. 4e reveal that the ZC nanofibers consist of a carbon matrix with embedded crystalline ZrC phases. The ZrC nanoparticles are dispersed as irregular speckles within the nanofibers, forming a Turing-like pattern. The formation of this Turing-type structure can be attributed to a diffusion-reaction dominated phase separation mechanism during the carbonization of the precursor. During the pyrolysis process, the different diffusion rates of the carbon source and zirconium lead to the spontaneous formation of periodic distributions of ZrC nanoparticles within the continuous carbon phase [19]. Furthermore, a detailed analysis was conducted on the grains dispersed in the nanofibers. As shown in Fig. 4b, the grains exhibit a typical "core-rim" architecture, comprising a crystallized core and an outer transition layer. Fig. 4c provides a detailed view of the edge region of a grain, where a distinct difference in crystallinity is evident between the core and the rim. The low-crystallinity rim layer measures approximately 2.51 nm in thickness [20]. Lattice fringes visible in the high-resolution image of the core region indicate the feature of ZrC (Fig. 4d). According to the EDS mapping results of the grain (Fig. 4f), the intensity of the Zr signal is significantly lower in the rim layer than in the core, while carbon remains relatively uniformly distributed. This suggests that the transition layer is likely composed of low-crystallinity ZrC and amorphous carbon. Fig. 4 g presents a HAADF-STEM image of the core region, where bright spots correspond to Zr atomic columns and dark regions represent carbon atoms [21-22]. The STEM-EDS elemental mappings in Figs. 4h-4i corroborate the distribution of carbon and zirconium at the atomic scale, showing high consistency with the ZrC crystal structure. The "core-rim" structure of individual particles and the Turing patterns with the nanofibers both originate from the non-equilibrium growth process. The different diffusion rates not only determine the morphology of the individual ZrC -based particles but also drive the formation of the unique Turing-type architecture of ZC nanofibers.

Further analysis was performed on the morphology and microstructure of the ZCO-600-5 nanofibers obtained through oxidation of the ZC nanofibers. As shown in the bright-field image (Fig. 5a), the resulting ZCO nanofibers exhibit a nanofibers morphology with an average diameter of approximately 440 nm, covered with numerous particulate protrusions on the surface. EDS elemental mapping (Fig. 5b) confirms the homogeneous distribution of Zr and O elements within the amorphous carbon matrix [23]. HRTEM images (Figs. 5c and 5d) clearly reveal the presence of tetragonal ZrO₂(t-ZrO₂) crystalline regions within the nanofibers. Lattice fringes with a spacing of 0.175 nm, corresponding to the (200) planes of t-ZrO₂, are visible in Fig. 5d [19]. The cross-sectional structure (Fig. 5e) indicates that the nanofibers consist of discrete particles embedded in a continuous matrix, inheriting the Turing-type architecture of the ZC precursor (Fig. 5g). Cross-sectional EDS (Fig. 5f) also reveals the nanofibers morphology, with ZrO₂ particles uniformly dispersed in the carbon matrix. High-resolution TEM image shows that the "core-rim" structure originally present in the ZC nanofibers disappears after oxidation (Fig. 5h). The ZrO₂ grains contain both amorphous regions and crystalline t-ZrO₂ phases, with lattice spacings of 0.312 nm and 0.187 nm corresponding to the (101) and (112) planes, respectively (Fig. 5i). The continuous carbon matrix also exhibits an amorphous/nanocrystalline mixed structure (Fig. 5k). Quantitative analysis via FFT and autocorrelation function indicates that the crystal lattice order (CLO) [24] values for the ZrO₂ grains and the carbon matrix are 64% and 9%, respectively (Figs. 5j and 5l), suggesting an abundance of amorphous/nanocrystalline heterogeneous interfaces within the Turing-patterned units.

The electromagnetic microwave absorption parameters of the nanofibers before and after oxidation were measured using a vector network analyzer [25]. The reflection loss ( RL ) values under different matching thicknesses were calculated based on transmission line theory and Equations (1) and (2):

where Z_in  denotes the input impedance, Z₀ is the impedance of free space, f is the frequency, c is the speed of light and d is the sample thickness. A lower RL value indicates stronger microwave absorption capability. An RL value of -10 dB is generally regarded as the effective absorption threshold, implying that 90% of the incident wave is absorbed [26]. The corresponding frequency range is defined as the effective absorption bandwidth ( EAB ). An ideal microwave absorber should exhibit a more negative RL value and a wider EAB. Figs. 6a-6f present the EMW absorption properties of ZC nanofibers and ZCO nanofibers prepared under different oxidation temperatures and durations with a loading ratio of 5wt.%. As shown in Fig. 6a, the ZC nanofibers show limited absorption performance, with a minimum reflection loss ( RL_min  ) of only 9.45 dB at a thickness of 4.99 mm. In contrast, the ZCO-600-5 sample, as anticipated from earlier structural analysis, demonstrates outstanding absorption characteristics. It achieves an RL_min  of -59.20 dB at a matching thickness of 2.39 mm, along with a maximum effective absorption bandwidth ( EAB_max  ) of 5.84 GHz (covering 11.48-17.32 GHz). Samples subjected to either insufficient or excessive oxidation failed to attain comparable performance.

In EMW absorption, the complex permittivity ε_r(ε_r=ε^'-jε^'') and complex permeability μ_r(μ_r=μ^'-jμ^'') play critical roles. The real parts ( ε^' and μ^' ) represent the ability to store electromagnetic energy, while the imaginary parts ( ε^'' and μ^'' ) reflect the dissipation capability. The dielectric and magnetic loss capacities can be quantitatively characterized by the dielectric loss tangent $\left(\mathrm{t}\mathrm{a}\mathrm{n}{\delta }_{\mathrm{e}}={\epsilon }^{\text{'}\text{'}}/{\epsilon }^{\text{'}}\right)$ and magnetic loss tangent $\left(\mathrm{t}\mathrm{a}\mathrm{n}{\delta }_{\mathrm{m}}={\mu }^{\text{'}\text{'}}/{\mu }^{\text{'}}\right)$, respectively. Both ZC and ZCO nanofibers are dielectric-dominated materials, with nearly constant μ_r values (μ^'≈1,μ^''≈0) [27]. Therefore, dielectric loss constitutes the primary mechanism for electromagnetic energy dissipation in these materials, primarily encompassing conduction loss and polarization loss. Fig. 7 shows the frequency-dependent complex permittivity and dielectric loss tangent ( $\mathrm{t}\mathrm{a}\mathrm{n}{\delta }_{\mathrm{e}}$ ) of both types of nanofibers [28]. Compared with ZC nanofibers, the introduction of lowpermittivity ZrO₂ in ZCO nanofibers results in lower values of both ε^' and ε^'' (Figs. 7a and 7d) [29]. The gradual decrease in ε^' with increasing frequency indicates typical dielectric dispersion behavior, suggesting the presence of dipole polarization [30-31]. This is primarily attributed to the relaxation that occurs when the dipoles within the sample fail to respond synchronously to the frequency variations of the alternating electromagnetic field [32]. According to Debye theory, ε^'' is closely related to electrical conductivity [25]. The incorporation of ZrO₂ reduces the originally excessive electrical conductivity of ZC, leading to an overall decrease in ε^''. The dielectric loss tangent are plotted in Figs. 7a and 7d. The ZC nanofibers exhibit a relatively high tan ${\delta }_{\mathrm{e}}$ value, indicating their strong capability for dielectric loss [29]. To gain deeper insight into the internal dielectric loss mechanisms, the Cole-Cole semicircle trends for ZCO nanofibers are plotted according to the Debye theory and presented in Fig. S6, where each relaxation process corresponds to a semicircular arc, indicative of distinct dielectric relaxation events [33]. In the Cole-Cole plots (Fig. S6), all samples except ZCO-700-5 exhibit an extended tail in the low-frequency region, indicative of significant conduction loss resulting from high electrical conductivity [34]. Meanwhile, all samples display depressed semicircular arcs, revealing the coexistence of multiple polarization loss mechanisms in the nanofibers arising from various relaxation processes, including interfacial and dipolar polarization [35]. Interfacial polarization originates from the numerous heterogeneous interfaces induced by the Turing-like structures, whereas dipolar polarization is associated with defects and oxygen containing functional groups introduced during the oxidation process. These defects serve as polarization centers, promoting dipole formation and subsequent polarization. Furthermore, under an alternating electromagnetic field, the oxygen-containing functional groups and inherent magnetic moments within the material undergo continuous oscillation and internal friction, thereby enhancing dipolar polarization loss [36].

The impedance matching characteristics and attenuation capabilities of EMW absorbing materials are of critical importance. The impedance matching characteristic is commonly evaluated using the normalized input impedance modulus $\left(\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|\right)$, which can be calculated by Eq. (1). Generally, $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ values ranging from 0.8 to 1.2 are considered optimal for achieving effective impedance matching [37]. When $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ approaches 1, optimal impedance matching is achieved, indicating minimal reflection of EMWs at the material surface and maximum penetration into the material for dissipation. On the other hand, the attenuation constant (α) is used to quantify the ability to attenuate EMWs, as derived from Eq. (3).

Figs. 8a-8f present the two-dimensional impedance matching $\left(\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|\right)$ profiles of ZC nanofibers and ZCO nanofibers obtained under various oxidation conditions. Although the $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ value exhibits an overall increasing trend with oxidation, this trend does not indicate that excessive oxidation improves impedance matching. An increase in ZrO₂ content will enhance the penetration of EMWs into the material. For instance, the ZCO-700-5 sample exhibits a sharp decline in electrical conductivity due to increased ZrO₂ content and severe consumption of the carbon matrix. As a result, EMWs penetrate the material without being effectively absorbed. Moderate oxidation proves beneficial in optimizing impedance matching. As illustrated in Fig. 8b, ZCO-600-5 demonstrates excellent impedance matching characteristics, with $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ approaching 1 across a broad frequency range. A large matching region is observed, and the bandwidth corresponding to the $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ range of 0.8-1.2 reaches 5.92 GHz (11.417.32 GHz ) at a specific thickness.

The attenuation constant ( α ) reflects the capability of a material to attenuate EMWs. As shown in Fig. 8h, the value of α exhibits a decreasing trend with the increasing oxidation degree. Although the ZC sample exhibits the highest attenuation constant (Fig. 8h), its poor impedance matching restricts overall absorption performance [38]. In contrast, the ZCO-700-5 sample exhibits the highest impedance matching and the lowest attenuation constant. As a result, EMWs can readily penetrate the material without being effectively absorbed [16]. Therefore, the key challenge lies in achieving a balanced control of $\left|{Z}_{\text{in}\text{ }}/{Z}_{0}\right|$ and α for high-performance EMW absorption. The ZCO-600-5 sample exhibits optimal impedance matching and a moderate attenuation constant, the favorable synergy between these two factors endows the material with outstanding EMW absorption performance.

These findings indicate that the moderate introduction of amorphous and nanocrystalline ZrO₂ not only provides an effective means for tuning impedance matching but also, together with the Turing-like structure that enhances interfacial polarization via abundant heterogeneous interfaces, contributes to superior EMW absorption performance. Consequently, the superior EMW absorption performance of ZCO-600-5 is attributed to the synergistic effect of excellent impedance matching and moderate attenuation capability, ultimately achieving a wide effective absorption bandwidth and strong absorption performance, meeting the requirements for high efficiency EMW absorption materials [39].

Furthermore, the absorption mechanism was analyzed using the quarter wavelength theory (Fig. 8i). The calculation formula is presented in Eq. (4). This theory indicates that when the material thickness satisfies specific matching conditions, incident and reflected waves interfere destructively, converting electromagnetic energy into thermal energy. Compared with ZC nanofibers and other ZCO nanofibers samples (Fig. S7), the close agreement between the experimental matching thickness of ZCO-600-5 and theoretical predictions confirms the dominance of this mechanism [31].

Fig. 9a provides a detailed summary of the EMW absorption mechanisms of the Turing-structured ZrO₂/C nanofibers. Firstly, the introduction of low-dielectricconstant ZrO₂ optimizes the impedance matching of the ZrO₂/C nanofibers by modulating the dielectric constant, allowing more EMWs to penetrate and be absorbed within the material. Secondly, the multi-scale 3D conductive network formed by the amorphous/nanocrystalline ZrO₂ and the carbon matrix nanofibers substrate facilitates electron hopping, thereby inducing conduction loss and converting EMW energy into Joule heat [40]. Finally, beyond the primary Turing structure comprising ZrO₂ particles embedded in the carbon matrix, the basic building units of the Turing structure ( ZrO₂ grain and carbon matrix) exhibit an amorphous/nanocrystalline hybrid nature with abundant heterogeneous interfaces. These interfaces promote the accumulation and migration of free charges, significantly enhancing interfacial polarization and thus strengthening the dielectric loss capability of the nanofibers [41]. Moreover, the multiscale heterogeneous nanofibers structure facilitates multiple reflections of EMWs, prolonging and increasing the propagation path of incident waves. In summary, the strategic compositional and structural design achieved a synergistic effect between optimized impedance matching and enhanced attenuation in the ZCO-600-5 sample, leading to exceptional EMW absorption performance, which surpasses that of most conventional nanofiber materials (Fig. 9b).

CST Studio Suite 2022 was employed to simulate the far-field radar wave interaction with the actual materials. A single-layer substrate model, comprising the sample coated on a Perfect Electric Conductor (PEC) base, was constructed (Fig. S8). The EMW absorption performance under practical application conditions was evaluated by comparing the reduction in radar cross-section (RCS) at various incident angles [42]. When the EMW-absorbing material is applied to a target surface, its strong absorption significantly attenuates the reflected RCS signal, indicating enhanced radar stealth capability [30,43]. As shown in Fig. 10a, with incident waves along the Z-axis, the RCS distribution intensity of the ZCO-600-5 sample is markedly lower than that of the ZC sample and those processed under other oxidation conditions (Fig. 10b), suggesting that ZCO-600-5 dissipates more incident EMW energy. This implies that in real-world scenarios, a larger proportion of radar waves would be absorbed by this material. The 2D radar imagery and corresponding RCS data (Figs. 10c and 10d) further confirm that ZCO-600-5 achieves the lowest RCS values, specifically demonstrating reductions of 34.94 dB m² at 0^∘ and 21.55 dB m² at 30^∘ incidence [44]. These simulation results are highly consistent with the measured EMW absorption properties, strongly demonstrating the excellent performance and promising potential of ZCO-600-5 for radar stealth applications.