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Realization of ferromagnetic graphene oxide with high magnetization by doping graphene oxide with nitrogen


The long spin diffusion length makes graphene very attractive for novel spintronic devices and thus has triggered a quest for integrating the charge and spin degrees of freedom. However, ideal graphene is intrinsic non-magnetic, due to a delocalized π bonding network. Therefore, synthesis of ferromagnetic graphene or its derivatives with high magnetization is urgent due to both fundamental and technological importance. Here we report that N-doping can be an effective route to obtain a very high magnetization of ca. 1.66 emu/g and can make graphene oxide (GO) to be ferromagnetism with a Curie-temperature of 100.2 K. Clearly, our findings can offer the easy realization of ferromagnetic GO with high magnetization, therefore, push the way for potential applications in spintronic devices.


Chemical doping is a fascinating way to intrinsically modify and improve graphene's physical and chemical properties. Notably, among the potential dopants, N atom is considered as an excellent candidate because it has comparable atomic size and contains five valence bonds with carbon atoms1. Nowadays, N-doped graphene (NG) has attracted much attention because of its excellent performance in electrocatalytic activity, electrical, fuel cells and optical properties, etc2,3,4. Notably, magnetism of graphene and its derivatives is of particular interest since the light weight magnets could open up new ways to design adaptable and flexible information storage systems5. Especially, the greatly potential application of graphene-based magnets in spintronics is promising, since graphene has extraordinary carrier mobility and may provide an easy way to integrate spin and molecular electronics6. The long spin diffusion lengths and coherent times arising from the weak spin-orbit and hyperfine interactions in graphene can provide ideal conditions for coherent spin manipulation which can act as the next-generation spintronic devices7. However, graphene is usually intrinsic non-magnetic and lacks of localized magnetic moments due to a delocalized π bonding network, which limits its applications in spintronic devices8.

Generally, point defects such as vacancies, zigzag edges, chemical doping of foreign atoms can induce localized magnetic moments in graphene, which is the preliminary of the existence of magnetic ordering9,10,11,12,13,14,15,16,17,18. It is demonstrated that high-density vacancies can make graphene fragile and lose its structural stability, by contrast, chemical doping can keep its structural stability and can introduce more point defects in graphene19,20. For example, fluorination of graphene can obtain a high magnetization up to 0.2 emu/g, one order higher than the maximum value of 0.02 emu/g induced by vacancies20. Up to now, the reported magnetic moment of graphene is still low and the distance between magnetic moments is long. As a result, these graphene materials always exhibit typically Curie-like paramagnetism20,21,22. Therefore, to combine charge and spin manipulation for the novel spintronic devices, it is urgent to develop effective methods for sythesizing ferromagnetic graphene with high magnetization. Note that, graphene oxide (GO) is usually considered as an insulator or a semiconductor. However, after chemical or thermal reduction, it can be zero-band-gap semi-metal graphene nanosheets23. Actually, after efficient reduction, the achieved mobility value of 5000 cm2 V−1 s−1 is close to that of mechanically cleaved graphene (ca. 10000 cm2 V−1 s−1)24. It has been demonstrated that annealing in ammonia can effectively reduce GO3, indicating its potential in spintronics.

Theoretical study confirmed that N-doping is an effective method to introduce magnetic moments into graphene25,26,27,28,29. In this study, we demonstrate that doping GO with N can obtain a very high magnetization (1.66 emu/g) and a significant increase of magnetization of GO (ca. 1509.1%). Most importantly, it makes the magnetism of GO from purely spin-half paramagnetism to ferromagnetism with Curie temperature (TC) of ca. 100.2 K.


Microstructures of GO and NGO

We prepared N-doped graphene oxide (NGO) by directly annealing GO in ammonia at 500°C. For GO, two factors have important influence on N content: few-layer ratio and O content of GO. It has been reported that compared to multi-layer GO, few-layer GO is more sensible to the adatoms and can be doped with higher N content30. It also has been confirmed that oxygen groups in GO favor the reactions with NH3 and C–N bond formation and directly annealing GO in ammonia can obtain high-content NGO31. Thus, to get GO with high few-layer ratio32, we centrifugated GO solution at 6000 rpm for 10 minutes and only collected GO dispersed in the brown supernatant for N-doping. To quantitatively analyze the layer number, we investigated GO by atomic force microscope (AFM). Shown in Fig. 1a is the typical AFM image. As indicated by the height images (inset of Fig. 1b), most of the heights of GO layers are ca. 1 nm. Based on the fact that the height may increase because of the trapped solvent and the folds between GO and the substrate, one can expect that most of the GO sheets are single- or bi-layer6. Shown in Fig. 1b is a typical transmission electron microscope (TEM) image of GO. One can find that the GO sheets are not well flat and look like wrinkled or crumpled thin papers with the size of several micrometers. To detect the O content of GO, we performed the X-ray photoelectron spectrum (XPS) measurement. As shown in Fig. 1c, the XPS spectrum of GO indicates that O content of GO defined as 100 O/C at.% is 48.37 at.%, indicating that the O content is high. Namely, we have synthesized GO with high few-layer ratio and O content.

Figure 1

Microstructure of GO and NGO.

(a) Tapping mode AFM height image of GO. Inset: The corresponding height profiles of the white lines with colorful crosses. The colorful arrows correnspond to the colorful crosses. (b) TEM image of GO. (c) XPS spectra of GO and NGO over a wide range of binding energies (0–1000 eV). (d) Fine-scanned N 1s XPS spectrum of NGO. The olive dots and red lines are measured dots and fitting curves.

Moreover, to detect the contents of O and N and bonding environment of C and N species of NGO, we also performed the XPS measurement. As shown in Fig. 1c, the XPS spectrum of NGO reveals that the O content which also defined as 100 O/C at.% is 6.59 at.%, much lower than that of GO. It demonstrates that a considerable amount of oxygen-containing functional groups were removed during annealing, which may be due to the formation of C–N bonds and reduction effects of thermal annealing in ammonia3,31. Moreover, it is found that compared to GO, NGO shows a clear N signal at ca. 400 eV. Shown in Fig. 1d is the high-resolution XPS spectrum in the N 1s binding energy range of NGO, which was deconvoluted into three subpeaks. The three subpeaks located at 398.3, 400.0 and 401.4 eV are attributed to pyridinic-like (N-6), pyrrolic-like (N-5) and graphitic-like (N-Q) atoms, respectively3,33. Based on the XPS results, the content of the N defined as 100 N/C at.% of NGO can be calculated to be 8.80 and the contents of N-6, N-5 and N-Q types are 3.45, 4.00 and 1.35 at.%, respectively. In other words, we have synthesized NGO with high N content by annealing GO with high few-layer ratio and O content.

Analysis of the spin-half paramagnetism of GO

We first carefully measured magnetic properties GO. Shown in Fig. 2a is the dependence of susceptibility χ = M/H on temperature T and it fits well with the Curie law χ = C/T. Inset is the corresponding 1/χ − T curve, which demonstrates a linear, purely Curie-like paramagnetic behavior, a solid evidence of the existence of localized magnetic moment. As shown in Fig. 2b, no significant ferromagnetic signal is observed even at 2 K. The MH curve is well fitted using the Brillouin function

Where x = gJμBH/(kBT), MS = NgJμB, kB the Boltzmann constant, N the number of present magnetic moments, J the angular momentum number and g is the Landau factor which is assumed to be 2. As shown by the fitting curve, the Brillouin function provides good fits for J = S = 1/2. The intrinsic spin-half paramagnetism agrees well with the existing theories for the contributions of point defects such as vacancies, adatoms and edges20,34,35. Also by fitting the curve, Ms can be obtained which is 0.11 emu/g, similar to the value reported21.

Figure 2

Magnetic properties of GO measured by a superconducting quantum interference device (SQUID) magnetometer.

(a) Typical χ − T curve measured from 2 to 300 K under the applied field H = 3 kOe. Inset is the corresponding 1/χ − T curve. Red symbols are the measurements and black solid line is fitted by the Curie law. (b) MH curve measured at 2 K. Red symbols are the measurements and black solid curve is fit to the Brillouin function with g = 2 and J = 1/2.

Magnetic properties of NGO

Subsequently, we carried out the magnetic measurements for NGO. Note that no positive magnetic signal and only purely diamagnetism can be observed in both GO and NGO at 300 K (Supplementary Fig. S1). Figure 3a shows the typical mass magnetization (MH) curve of NGO measured at 2 K. One can find that the coercive field (Hc) and remnant magnetization (Mr) are 160 Oe and 0.039 emu/g (inset of Fig. 3a), a solid evidence for ferromagnetism. Subsequently, we performed the MT measurement of NGO and found a clear TC at ca. 100.2 K (Fig. 3b), implying that the Tc is above liquid N2 temperature of 77 K. It also can be confirmed by the two MH curves measured at 80 and 110 K (Fig. 3c).

Figure 3

Magnetic properties of NGO measured by SQUID.

(a) Typical MH curve measured at 2 K. Inset is a part of the magnetization curve. (b) MT curve of NGO measured from 2 to 300 K under the applied field H = 500 Oe. (c) MH curves of NGO measured at 80 and 110 K. Inset is a part of the magnetization curves.

It is found that the MT curve of NGO shows typically paramagnetic behavior at low temperature below 8 K (Fig. 3b). Namely, the magnetism at 2 K is composed of two parts: paramagnetism and ferromagnetism, which can be expressed as Mtotal = Mpara + Mferro. Considering the fact that ferromagnetic mass magnetization can saturate at a high applied field, one have to set paramagnetic M0 of the sample as 1.39 emu/g and J as 1.11 to fit the curve by Brillouin function (Fig. 4). As reported, J can be 0.5, 1, or 2.5, etc., which generally should be the integral multiple of 0.5 and corresponds to magnetically coupled unpaired electrons20,21,22. However, the magnetic structure of our sample may be uneven and different J may exist in different sheets in NGO. For example, some of sheets show J = 0.5 and some show J = 1, or 1.5. Therefore, as an average, the total J may become 1.11. Moreover, theoretically, the N atom can induce a net magnetic moments of 1.8, 0.95, or 0.67 μB for specific structures25,29. It also may be the reason that J = 1.11 in NGO. By subtracting the paramagnetic signal from the observed data, one can obtain the remaining ferromagnetic moment. The magnetization is approximately saturated at 6 kOe (inset of Fig. 4) and the saturation magnetization of ferromagnetic signal is ca. 0.27 emu/g at 2 K. We should note that the issue of the minute magnetic contaminant in the sample is very important because trace ferromagnetic impurites also can contribute to the ferromagnetic signal observed36,37. Therefore, we have very carefully analyzed the magnetic impurities of NGO by inductively coupled plasma (ICP) analysis (Supplementary Table S1). Clearly, the results showed that the magnetic impurity elements (such as Fe, Co, Ni or Mn) of NGO are below 10 ppm, demonstrating that NGO is highly pure and the contribution of magnetic impurities is neglectable. Actually, the ferromagnetic signal of ca. 0.27 emu/g is equivalent to 1277 ppm Fe, ca. 284 times higher than the ICP result. Clearly, the contribution of magnetic impurities is neglectable. From M0 added with saturated ferromagnetic magnetization, one can calculate the Ms of NGO is ca. 1.66 emu/g. To best of our knowledge, it is the highest intrinsic magnetization reported for all graphene materials. Interestingly, N-doping increases the magnetization of GO from 0.11 to 1.66 emu/g, a significant increase of ca. 1509.1%. It is clear that N-doping results in the increase of the magnetization of GO and the generation of ferromagnetism.

Figure 4

Analysis of the 2 K MH curve of NGO.

Black curve is the measured curve and blue line is the fitting curve for paramagnetism by the Brillouin function with g = 2 and J = 1.11. Red curve is ferromagnetic mass magnetization by subtracting the paramagnetism from the measured curve. Inset is a part of the ferromagnetic mass magnetization.


Actually, the contribution of different structural defects like vacancies and O for magnetization in GO and NGO may be different. Especially, the O content is relatively high and the difference of O contribution in GO and NGO is highly possible38,39. Approximately, to make a simple comparison with the results of NGO, we obtained GO samples (GO-a300, GO-a500, GO-a700 and GO-a900, numeric numbers denote the annealing temperature) by annealing GO in Ar. Based on the XPS results, the O contents defined as 100 O/C at.% are in the range of 5.7–13.35 at.% in annealed GO samples (Supplementary Table S2). The magnetic results show that all of the annealed GO samples are spin-half paramagnetic with a low magnetization similar to GO (Supplementary Fig. S2), one order of magnitude lower than that of NGO. Thus, it is reasonable to assume that the contribution of O to the significant increase of the magnetization and the generation of ferromagnetism in NGO is negligible.

Theoretical calculation showed that localized magnetic moments can be induced by different types of N atoms25,26,27,28,29. As proposed by Zhang et al., a combination of vacancy defects and N atoms may provide a unique way for enhancing the magnetic moment28. Especially, N-5 atom plays the important role in the introduction of magnetic moments because a N-5 atom can introduce a net magnetic moment of 0.95 μB at either the edge or defect because of the contribution of the π bonds25,27. By contrast, N-Q atom was considered to support no magnetic moment, however, it may act as a stable attractor, forming a magnetic defect complex N-Q + C-ad, which can contribute magnetic moment of 0.98 μB26. Considering that O content in our NGO is relatively high, the formation of N-Q + O-ad may be highly possible29. Thus, we cannot exclude the contribution from N-Q. We note that the specific contribution by each specific type of the three N types is complicated and it is difficult to clarify the specific contribution in NGO. Moreover, the magnetic coupling between the localized magnetic moments is the preliminary of the existence of ferromagnetic ordering. Notably, after reduction, GO can transform from an insulator to a graphene-like semi-metal40. Thus, the magnetic coupling between the magnetic moments may appear via Ruderman–Kittel–Kasuya–Yosida (RKKY) interactions by delocalized π electrons, which is expected to decay as Dr, where D is the distance between the magnetic moments and r is the decay exponent41,42. It has been confirmed that graphene with low magnetization exhibits pure Curie-like paramagnetism due to the long distance between magnetic moments20,21. In our NGO, it is reasonable to assume that with the increasing of localized magnetic moments of GO from 3.89 to 42.48 μB per 10000 C atoms because of N-doping, the distance between the magnetic moments will decrease. As to the decay exponent r, it has been proposed that with the enhancing of electron-electron interaction, r may decrease and the power-law decay becomes more long ranged43. Different from the case of fluorination which makes the Fermi level shift downward19,44, N-doping can make the Fermi level shifted upward due to the extra π electrons and make graphene electron-rich45. Thus, N-doping can enhance the magnetic coupling between the magnetic moments because of the decrease of distance and decay exponent.

Despite that the RKKY interaction usually occurs in metallic material, the bound magnetic polarons (BMPs) may also generate ferromagnetism in semiconductors. In short, the ferromagnetic coupling is mediated by shallow donor electrons that form BMPs, which overlap to create a spin-split impurity band46. For example, oxygen vacancies can act as BMPs and trap free electrons and the electrons trapped in these BMPs tend to get easily polarized under the influence of the magnetic field and, resulting in ferromagnetism47. Similarly, in NGO, the N atoms may act as BMPs thanks to the strong electron affinity48. We note that the exact ferromagnetic coupling mechanism is not clear at present and need to be confirmed by more experimental and theoretical work.

Additionally, we obtained NGO-a700 and NGO-a900 by annealing NGO in Ar at 700 and 900°C and found that annealing-dependence magnetic properties support this law. In short, annealing NGO resulted in the decreasing in N content (Supplementary Table S3), magnetiztion and Tc (Supplementary Figs. S3 & S4). The localized magnetic moments also can be induced by F or H atoms, however, H and F atoms have a strong tendency towards clustering or even lose at relatively low temperatures44,49. Our results indicates that NGO can has relatively high stability in both structure and magnetic properties, thus, N-doping provides a good candidate for H- and F-doping.

Anyway, we successfully demonstrated that N-doping can make GO to be ferromagnetic with a very high magnetization of 1.66 emu/g and an above liquid N2-temperature TC of ca. 100.2 K. Thus, our method offers the easy fabrication of ferromagnetic GO with high magnetization, therefore, pushes the way for potential applications in magnetic graphene.


Sample preparation

GO was synthesized by chemical exfoliation of natural flake graphite powder (500 mesh). The solution of GO was first centrifugated at 6000 rpm for 10 min and the brown supernatant was collected to get few-layer GO. To obtain highly pure GO sample, GO was washed with hydrochloric acid for 15 times and then with ethanol for 10 times. Thereafter, NGO was obtained by annealing GO at 500°C for 3 h in ammonia (~99%) under ambient pressure.

Structural characterization and magnetic measurements

The morphologies of the samples were investigated by TEM (model JEM–2100, Japan) and AFM (Veeco dimension V, USA). For quantitative determination of the chemical composition and the bonding environment of the samples, XPS were measured on PHI5000 VersaProbe (ULVAC-PHI, Japan) using Al Ka radiation. The magnetic properties of the samples were measured using SQUID magnetometer with a sensitivity of less than 10−8 emu (Quantum Design MPMS–XL, USA) and all data have been corrected for the diamagnetic contribution by subtracting the corresponding linear diamagnetic background measured at RT. The magnetic impurity elements (such as Fe, Co, Ni or Mn) of all the samples are below 10 ppm measured by ICP spectrometry (Jarrell–Ash, USA).


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This work was supported by the State Key Program for Basic Research (Grant Nos. 2012CB932304 and 2010CB923402) and NSFC (Grant Nos. U1232210 and 51072079), P. R. China.

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N.J.T. proposed and supervised the project, Y.L. and N.J.T. designed the experiments, Y.L. carried out the experiments, Y.L., N.J.T. and X.G.W. analyzed the data and wrote the manuscript. Q.F., M.L., Q.H.X., F.C.L. and Y.W.D. had valuable discussions and edited the manuscript. All the authors commented on the manuscript.

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Liu, Y., Tang, N., Wan, X. et al. Realization of ferromagnetic graphene oxide with high magnetization by doping graphene oxide with nitrogen. Sci Rep 3, 2566 (2013).

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