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.

C hemical 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 atoms 1 . Nowadays, N-doped graphene (NG) has attracted much attention because of its excellent performance in electrocatalytic activity, electrical, fuel cells, and optical properties, etc [2][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 systems 5 . 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 electronics 6 . The long spin diffusion lengths and coherent times arising from the weak spinorbit and hyperfine interactions in graphene can provide ideal conditions for coherent spin manipulation which can act as the next-generation spintronic devices 7 . However, graphene is usually intrinsic non-magnetic and lacks of localized magnetic moments due to a delocalized p bonding network, which limits its applications in spintronic devices 8 .
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 ordering [9][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 graphene 19,20 . 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 vacancies 20 . 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 paramagnetism [20][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 nanosheets 23 . Actually, after efficient reduction, the achieved mobility value of 5000 cm 2 V 21 s 21 is close to that of mechanically cleaved graphene (ca. 10000 cm 2 V 21 s 21 ) 24 . It has been demonstrated that annealing in ammonia can effectively reduce GO 3 , indicating its potential in spintronics.
Theoretical study confirmed that N-doping is an effective method to introduce magnetic moments into graphene [25][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 (T C ) of ca. 100.2 K.

Results
Microstructures of GO and NGO. We prepared N-doped graphene oxide (NGO) by directly annealing GO in ammonia at 500uC. 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 content 30 . It also has been confirmed that oxygen groups in GO favor the reactions with NH 3 and C-N bond formation, and directly annealing GO in ammonia can obtain highcontent NGO 31 . Thus, to get GO with high few-layer ratio 32 , 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-layer 6 . 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.
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 ammonia 3,31 . 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, respectively 3,33 . 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 fewlayer 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 x 5 M/H on temperature T and it fits well with the Curie law x 5 C/T. Inset is the corresponding 1/x 2 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 M 2 H curve is well fitted using the Brillouin function Where x 5 gJm B H/(k B T), M S 5 NgJm B , k B 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 5 S 5 1/2. The intrinsic spin-half paramagnetism agrees well with the existing theories for the contributions of point defects such as vacancies, adatoms, and edges 20,34,35 . Also by fitting the curve, M s can be obtained which is 0.11 emu/g, similar to the value reported 21 .
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 (M 2 H) curve of NGO measured at 2 K. One can find that the coercive field (H c ) and remnant magnetization (M r ) are 160 Oe and 0.039 emu/g (inset of Fig. 3a), a solid evidence for ferromagnetism. Subsequently, we performed the M 2 T measurement of NGO and found a clear T C at ca. 100.2 K (Fig. 3b), implying that the T c is above liquid N 2 temperature of 77 K. It also can be confirmed by the two M 2 H curves measured at 80 and 110 K (Fig. 3c). It is found that the M 2 T 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 M total 5 M para 1 M ferro . Considering the fact that ferromagnetic mass magnetization can saturate at a high applied field, one have to set paramagnetic M 0 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 electrons [20][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 5 0.5, and some show J 5 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 m B for specific structures 25,29 . It also may be the reason that J 5 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 observed 36,37 . Therefore, we have very carefully analyzed the magnetic impurities of NGO by inductively coupled plasma (ICP) analysis    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 M 0 added with saturated ferromagnetic magnetization, one can calculate the M s 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 Ndoping results in the increase of the magnetization of GO and the generation of ferromagnetism.

Discussion
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 possible 38,39 . 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 atoms [25][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 moment 28 . 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 m B at either the edge or defect because of the contribution of the p bonds 25,27 . 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 1 C-ad, which can contribute magnetic moment of 0.98 m B 26 . Considering that O content in our NGO is relatively high, the formation of N-Q 1 O-ad may be highly possible 29 . 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-metal 40 . Thus, the magnetic coupling between the magnetic moments may appear via Ruderman-Kittel-Kasuya-Yosida (RKKY) interactions by delocalized p electrons, which is expected to decay as D 2r , where D is the distance between the magnetic moments and r is the decay exponent 41,42 . It has been confirmed that graphene with low magnetization exhibits pure Curie-like paramagnetism due to the long distance between magnetic moments 20,21 . In our NGO, it is reasonable to assume that with the increasing of localized magnetic moments of GO from 3.89 to 42.48 m B 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 ranged 43 . Different from the case of fluorination which makes the Fermi level shift downward 19,44 , N-doping can make the Fermi level shifted upward due to the extra p electrons, and make graphene electron-rich 45 . 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 band 46 . 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 ferromagnetism 47 . Similarly, in NGO, the N atoms may act as BMPs thanks to the strong electron affinity 48 . 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 900uC, 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 T c (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 temperatures 44,49 . 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 N 2 -temperature T C 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.

Methods
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 500uC 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 28 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).