Introduction

Boron nitride (BN) is a new type of ceramic material with excellent performance and great potential for development. Due to its low dielectric constant1, wave transparency2,3, good electrical insulation4, low thermal expansion5, high thermal conductivity6, high-temperature lubricity7, high-temperature stability8, and wide band gap9. Common BN contains hexagonal boron nitride (h-BN) with a graphite layered structure, cubic boron nitride (c-BN) with a diamond sphalerite structure, wurtzite boron nitride (w-BN) with a hexagonal diamond wurtzite structure, rhombohedral boron nitride (r-BN) with a trigonal phase graphite structure, turbostratic boron nitride (t-BN) with a laminar structure, and amorphous boron nitride10,11,12,13,14,15. Of these, r-BN has high chemical stability and oxidation resistance, which makes it suitable for high-temperature resistant materials. Moreover, it also has a wide band gap, high thermal conductivity, and high resistivity, and can be used as an ideal substrate and heat sink material for high-power, high-temperature, and semiconductor materials.

At present, the research on BN is mainly focused on h-BN16,17,18,19,20 and c-BN21,22,23, and there has been little research on r-BN. In recent years, researchers have mainly used chemical vapor deposition (CVD) to synthesize r-BN. Chubarov et al. performed an in-depth study of r-BN. They used triethylboron and ammonia as precursors, and via CVD, r-BN was produced on a sapphire substrate at 1500 °C and a pressure of 7 kPa. The addition of a small amount of SiH4 to the gas mixture was also studied, and it was found that Si atoms acted as surface-active substances that stimulated the formation of high-quality r-BN24. Subsequently, they formed an AlN buffer layer by in-situ nitridation, and BN was grown under low pressure using H2 as a carrier gas at 1200–1500 °C25. After SiC was used as the substrate, it was found that growth temperature was 1500 °C, the N / B ratio was 642 and the deposition pressure was 7 kPa favored r-BN epitaxial growth, and no buffer layer was required26. In addition, Oku et al.27 prepared r-BN particles of 50–1000 nm diameter via CVD on a graphite substrate from a BCl3-NH3-H2 reaction system at 1600 °C and a total pressure of 3–5 Torr. Most of these methods require a high reaction temperature, a certain pressure, or a particular explosive atmosphere, and the purity of the synthesized r-BN is not high.

Other methods have also been used to prepare r-BN. Bao et al.28 prepared highly crystalline r-BN triangular nanosheets by using NaNH2 and B2O3 as raw materials in a solid-phase reaction in an autoclave at 600 °C for 6 h. The obtained r-BN triangular nanosheets had a width of approximately 300–500 nm and a thickness of approximately 50–90 nm, but this method required a long reaction time and a certain pressure. Ye et al.13 prepared r-BN powders by using Na2B4O7 and Mg as raw materials at 1000 °C for 3 h under a nitrogen atmosphere with NaCl molten salt. The prepared BN was not high in purity and it contained h-BN, and the reaction temperature was high. Therefore, further research is still needed to improve the production process of r-BN to obtain an r-BN preparation method that is simple and safe, uses a low synthesis temperature, and produces high yield.

In this work, we report on r-BN synthesized in a NaCl-KCl eutectic salt and a nitrogen atmosphere by using KBH4 and NH4Cl as the main raw materials, and compare the effect of the salt-free condition on the synthesis of r-BN. High-purity r-BN was synthesized at 650 °C and normal pressure by using the molten-salt synthesis (MSS)29,30,31,32,33,34 method, which was 250 °C lower than the temperature required when no salt was added, and it needed a shorter reaction time. The effect of reaction temperature on the phase and microstructure of r-BN was studied. In addition, the chemical valence, optical properties, and specific surface area of the as-prepared r-BN nanoflakes were also investigated. One possible formation mechanism of r-BN is put forward. Finally, the prepared r-BN nanoflakes were subjected to antioxidant analysis.

Methods

Preparation of r-BN nanoflakes

Potassium borohydride (KBH4, 97.0% purity, Shanghai Aladdin Biochemical Technology Co., Ltd.) and ammonium chloride (NH4Cl, 99.5% purity, Tianjin Kaitong Chemical Reagent Co., Ltd.) were used as the main raw materials; sodium chloride (NaCl, 99.5% purity, Shanghai Aladdin Biochemical Technology Co., Ltd.) and potassium chloride (KCl, 99.5% purity, Shanghai Aladdin Biochemical Technology Co., Ltd.) were used as the molten salt to synthesize r-BN in high-purity nitrogen (99.999%). The raw materials (KBH4/NH4Cl, molar ratio of 1:2) and molten salt (molar ratio of NaCl/KCl = 1:1) were mixed at a mass ratio of 6:5. The mixture was heated from 25 °C at a ramp of 2 °C/min to 300 °C in a vertical corundum tube furnace, and then heated to 650–1100 °C at a rate of 4 °C/min and held for 4 h. After that, the reaction products were cooled in the furnace to room temperature. The reaction products were soaked in distilled water for 2 h and washed with distilled water two to three times by using an ultrasonic cleaner to remove unreacted materials and molten salts. The final product was then dried at 110 °C to obtain r-BN nanoflakes.

Because NH4Cl would become volatile above 330 °C, the mixture was heated from 25 °C to 300 °C at a rate of 2 °C/min so that KBH4 and NH4Cl could produce more stable substances to reduce the loss in the subsequent NH4Cl heating process, and the amount of NH4Cl was greater than that of KBH4 to compensate for the loss of NH4Cl at high temperature.

The reaction for synthesizing BN can be described as follows:

$${{\rm{KBH}}}_{4({\rm{s}})}+{{\rm{NH}}}_{{\rm{4}}}{{\rm{Cl}}}_{({\rm{s}})}\to {{\rm{BN}}}_{({\rm{s}})}+{{\rm{KCl}}}_{({\rm{s}})}+{{\rm{4H}}}_{{\rm{2}}({\rm{g}})}$$
(1)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=-\,265.01-0.41{\rm{T}}\,({\rm{KJ}}\cdot {{\rm{mol}}}^{-1})$$

Characterization

The phases of the products were analyzed by X-ray diffraction (XRD, PANalytical, X’Pert Pro) using CuKα radiation. The element species and chemical valences of the samples’ surfaces were studied by X-ray photoelectron spectroscopy (XPS, Thermo Fisher Scientific, ESCALAB 250Xi) with AlKα radiation. The morphology and crystal structure were observed by scanning electron microscopy (SEM, FEI, Nova 400 Nano SEM), high-resolution transmission electron microscopy (HRTEM, JEOL, JEM-2100 UHR STEM/EDS) and atomic force microscopy (AFM, NT-MDT Prima). In addition, a synchronous thermal analyzer with thermogravimetric analysis-differential thermal analysis (TG-DTA, NETZSCH, STA449F3) was used to investigate the oxidation resistance of the as-prepared BN, and the generation process of the BN. The infrared absorption of the product was tested using the Fourier transform infrared (FTIR, Thermo Fisher Scientific, Nicolet iS 50) spectrum. The Brunauer–Emmett–Teller (BET) specific surface area of the as-prepared BN was characterized using a fully automatic surface area and porosity analyzer (JWGB, JW-BK100C).

Results and Discussion

Phase analysis

Figure 1a shows the XRD patterns of samples heated at different temperatures for 4 h in NaCl-KCl eutectic salts. At 650 °C, the diffraction peak of BN appeared at 25–30°, but the amount of BN obtained after water washing of the fired product was small. This is because the molten salt partially melted (the eutectic melting temperature of NaCl-KCl is 657 °C), and generated a small amount of liquid phase environment. The raw materials of KBH4 and NH4Cl were mostly evaporated or decomposed after a long time at low temperature. This indicates that an excessive holding time at low temperatures was not conducive to the synthesis of BN. As the heating temperature rose to 1100 °C, the main diffraction peak of BN became sharp, and the peak intensity was maximized. This shows that BN synthesized at 1100 °C had the best crystallinity. Furthermore, there are two diffraction peaks: the peaks at diffraction angles (2θ) of 26.717° and 42.620° can be indexed to r-BN ((003) and (101)), respectively. In addition, a small amount of O2 from the N2 gas caused slight oxidation of the BN during the synthesis. A weaker hump is found at a diffraction angle of 22°, which corresponds to amorphous B2O3.

Figure 1
figure 1

XRD patterns of samples heated at different temperatures for 4 h: (a) With salt; (b) Without salt.

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Figure 1b shows the XRD patterns of samples heated at different temperatures for 4 h without adding salt. No BN was generated at 800 °C. When the heating temperature was 900 °C, BN started to form. At 900–1100 °C, as the heating temperature increased, the peak intensity of BN increased and its peak became sharper. However, as the heating temperature rose to 1100 °C, the diffraction peak of the (003) crystal plane showed a slight shift in the higher angle direction, accompanied by a narrowing of the diffraction peak. Figure 1a also shows this phenomenon. According to the Bragg equation (\(2{\rm{d}}\,\sin \,\theta ={\rm{n}}\lambda \)), the diffraction peak is shifted to a larger angle, the lattice spacing of BN is decreased, and the lattice is shrunken along the c-axis orientation. The grain size is larger in the direction perpendicular to the (00 l) direction, resulting in a narrowing of the (003) peak by continuous X-ray scattering35. In addition, a small diffraction peak appears at an angle of 75.955°, which is the (110) crystal plane of r-BN.

XPS can be used to check all elemental information in a substance. Figure 2a shows the full spectrum of the product XPS. In Fig. 1a, the O1s peak (532.77 eV) is attributed to amorphous B2O3. The C1s peak (284.94 eV) is attributed to the addition of C as an internal standard substance. The binding energies of B1s and N1s are 190.75 eV and 398.09 eV, respectively. As shown in Fig. 2b, the B1s spectrum has two peaks at 191.42 eV and 192.04 eV, corresponding to B-N and B-O, respectively. Moreover, the N1s spectrum has a peak at 398.19 eV, corresponding to N-B36 (Fig. 2c). From the elemental content calculation of the XPS data (Table 1), the product consists of 91.87% BN and 8.13% B2O3.

Figure 2
figure 2

XPS spectra of BN synthesized at 1100 °C in NaCl-KCl eutectic salt: (a) The full spectrum of the product XPS; (b) B1s spectra of BN; (c) N1s spectra of BN.

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Table 1 The relative content of elements in the XPS spectra of Fig. 2.
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Microstructure analysis

Figure 3 shows SEM images of the BN synthesized at different temperatures in NaCl-KCl eutectic salts. Figure 3a shows many thin and poorly crystallized BN nanoflakes at 800 °C, which are stacked in a staggered relation to each other to form many small holes. The production of these holes may have been caused by the volatilization of the raw materials or the gases produced by the reaction. When the heating temperature rose to 900 °C, BN nanoflakes grew (Fig. 3b). At 1000 °C, the as-synthesized BN has a uniform morphology with a diameter of 200–300 nm and a thickness of 40–70 nm, and the two grains grow close together (Fig. 3c). As the heating temperature was increased to 1100 °C, the morphology of the BN was approximately unchanged, but some BN nanoflakes became curled (Fig. 3d). This may have occurred to reduce the surface free energy, so that the BN nanoflakes were in the lowest energy state to eliminate the internal stress of the flake structure. The nanoflake diameter is approximately 300–500 nm and the thickness is approximately 25–50 nm.

Figure 3
figure 3

SEM images of BN synthesized at different temperatures in NaCl-KCl eutectic salts: (a) 800 °C; (b) 900 °C; (c) 1000 °C; (d) 1100 °C.

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Figure 4 shows SEM images of the BN synthesized at different temperatures without adding salt. Figure 4a shows that irregular grains were generated at 800 °C, and the low temperature was not conducive to the growth of grains. Some irregular BN nanoflakes appear at 900 °C (Fig. 4b). When the temperature is 1000 °C, the BN nanoflakes are not uniform in size, and many small flake-like particles of BN are formed on the large flake-like BN, and the small flake-like BN has grown tightly together (Fig. 4c). As the temperature rose to 1100 °C, the flake-like BN grew to a diameter of approximately 400–700 nm, and a thickness of approximately 50–75 nm (Fig. 4d).

Figure 4
figure 4

SEM images of BN synthesized at different temperatures without adding salt: (a) 800 °C; (b) 900 °C; (c) 1000 °C; (d) 1100 °C.

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The effects of different temperatures on the morphology and crystal structure of BN formed in a molten-salt environment were further investigated by TEM (Fig. 5). Figure 5a shows that the BN is very thin, and has grown with a staggered profile, with an average thickness of approximately 10 nm at 700 °C. At 800 °C, the crystallinity of the BN is not good, and the BN nanoflakes have rough boundaries and disordered edges (Fig. 5b). At 900 °C, the tip of the generated BN is clearly bifurcated, which could be described as two grains of BN grown into one grain along the c-axis direction (Fig. 5c). At 1000 °C, the BN nanoflakes have grown closely together and are of uniform size (Fig. 5d), which is consistent with Fig. 3c, and this further shows that the morphology of the BN synthesized at 1000 °C is better.

Figure 5
figure 5

TEM images of BN synthesized at different temperatures in NaCl-KCl eutectic salts: (a) 700 °C; (b) 800 °C; (c) 900 °C; (d) 1000 °C.

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In addition, Fig. 6 shows the TEM, HRTEM, and selected area electron diffraction (SAED) images of BN synthesized at 1100 °C in NaCl-KCl eutectic salts. Figure 6a shows a typical TEM image of BN nanoflakes, which have a diameter of 70–130 nm and a thickness of 5–30 nm, and some BN nanoflakes are wrinkled. The inset in Fig. 6a shows the SAED pattern of r-BN with some diffraction spots distributed over the diffraction rings, indicating that the BN nanoflakes have a polycrystalline structure. The diffraction rings are indexed as the (003) and (101) planes of r-BN, which corresponds to the XRD results. Figure 6b is the HRTEM image of the BN in Fig. 6a. The lattice spacing of the BN in the smooth area is 0.34 nm, which corresponds to the (003) plane of r-BN (3.334 Å, ICDD No. 00-045-1171)13, indicating that the BN nanoflakes grew in a direction perpendicular to the (003) crystal plane. This directly confirms our interpretation of the phenomenon shown in Fig. 1. However, the lattice spacing at the fold is 0.35 nm. This may be due to the rotation of the lattice plane, which caused the BN nanoflakes to curl and exhibit folds on the crystal plane20, as in Fig. 3d.

Figure 6
figure 6

TEM and SAED (a), HRTEM (b) images of BN synthesized at 1100 °C in NaCl-KCl eutectic salts.

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The morphology of BN synthesized at 1100 °C in NaCl-KCl eutectic salts was further analyzed by AFM. The three-dimensional view and enlarged plan view of BN are shown in Fig. 7a,b. It can be clearly observed that BN has a flake-like structure, which is consistent with the previous SEM and TEM images (Figs 3d and 6a). The flakes are formed in a continuous step shape, the steps do not overlap each other, the surface is flat and smooth, and the width of the BN is approximately 400–450 nm. The elastic modulus of the BN is approximately 1.60 GPa (Fig. 7c).

Figure 7
figure 7

AFM images of BN synthesized at 1100 °C in NaCl-KCl eutectic salts: (a) Three-dimensional view; (b,c) Enlarged plan view.

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FTIR spectrum of r-BN

The FTIR spectrum of the BN synthesized at 650 °C and 1100 °C in NaCl-KCl eutectic salt is shown in Fig. 8. The BN synthesized at 650 °C shows two strong absorption peaks at 1377 cm−1 and 790 cm−1, which can be referred to as the in-plane B-N stretching vibration and the out-of-plane B-N-B bending vibration, respectively25. However, the BN synthesized at 1100 °C forms a weaker and broader absorption peak at 3428 cm−1, which may be due to the O-H bond of water adsorbed on the sample surface. The infrared analysis results are consistent with the XRD results, and this further confirms that the resulting product is high-purity r-BN.

Figure 8
figure 8

FTIR spectrum of the BN synthesized at 650 °C and 1100 °C in NaCl-KCl eutectic salt.

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Specific surface area analysis of r-BN

It is well known that the higher the specific surface area of a catalyst carrier, the more favorable the dispersion of the active components, and thus the more conducive to the improvement of its catalytic activity. Therefore, the high specific surface area of BN is of great value as a catalyst carrier37,38. With its high specific surface area, BN can be used not only as a catalyst carrier but also as an adsorbent and hydrogen storage material39,40,41. Figure 9 shows the specific surface area of BN synthesized at different temperatures, with and without salt. The synthesis temperature was 900–1100 °C, and the specific surface area of the BN synthesized by MSS42,43,44,45,46,47,48,49 method is 142.61–294.26 m2/g. The specific surface area of the BN synthesized at 1000 °C is the largest, at 294.26 m2/g. This shows that the BN particles produced at this temperature were smaller, as is further confirmed by Fig. 3b–d.

Figure 9
figure 9

Specific surface area of BN synthesized at different temperatures, with and without salt.

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When no salt was added, as the synthesis temperature increased, and the specific surface area of BN, which was in the range of 151.51–251.85 m2/g, decreased, indicating that as the temperature rose, the product particles grew. This is further confirmed by Fig. 4b–d. In addition, the two synthesis methods of BN were compared, and the specific surface area of the BN synthesized by the MSS method at 1000 °C was found to be the largest.

Reaction mechanism of r-BN

Figure 10 shows the TG-DTA curves of the raw materials heated from 25 °C at 5 °C/min to 1100 °C under a nitrogen atmosphere. The TG-DTA curves of the raw materials heated to 1100 °C in NaCl-KCl eutectic salts are shown in Fig. 10a. As the heating temperature increased, an endothermic peak appeared at 259 °C with the partial volatilization or decomposition of NH4Cl (Eq. 2). With the increase in heating temperature, there was a faint endothermic peak at 582 °C due to the decomposition of KBH4 (Eq. 3). During this process, the generated KH and HCl reacted to generate H2 (Eq. 4). An exothermic peak appeared at 775 °C, and the mass of the sample decreased with increasing temperature. The reason for this is that the resulting intermediate B3N3H6 (Eq. 5) was slowly dehydrogenated and became exothermic, resulting in the formation of BN (Eq. 6)50,51. The total weight loss was approximately 66%.

$${{\rm{N}}{\rm{H}}}_{4}{{\rm{C}}{\rm{l}}}_{({\rm{s}})}\to {{\rm{N}}{\rm{H}}}_{3({\rm{g}})}+{{\rm{H}}{\rm{C}}{\rm{l}}}_{({\rm{g}})}$$
(2)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=97.72-0.27{\rm{T}}\,({\rm{KJ}}\cdot {{\rm{mol}}}^{-1})$$
$${{\rm{KBH}}}_{{\rm{4}}({\rm{s}})}\to {{\rm{BH}}}_{{\rm{3}}({\rm{g}})}+{{\rm{KH}}}_{({\rm{g}})}$$
(3)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=377.28-0.26{\rm{T}}\,({\rm{KJ}}\cdot {{\rm{mol}}}^{-1})$$
$${{\rm{KH}}}_{({\rm{g}})}+{{\rm{HCl}}}_{({\rm{g}})}\to {{\rm{KCl}}}_{({\rm{s}})}+{{\rm{H}}}_{{\rm{2}}({\rm{g}})}$$
(4)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=-\,413.23+0.15{\rm{T}}(\mathrm{KJ}\cdot {{\rm{mol}}}^{-1})$$
$$3{{\rm{NH}}}_{{\rm{3}}({\rm{g}})}+3{{\rm{BH}}}_{{\rm{3}}({\rm{g}})}\to {{\rm{B}}}_{{\rm{3}}}{{\rm{N}}}_{{\rm{3}}}{{\rm{H}}}_{{\rm{6}}({\rm{g}})}+6{{\rm{H}}}_{{\rm{2}}({\rm{g}})}$$
(5)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=-\,642.95-0.02{\rm{T}}\,({\rm{KJ}}\cdot {{\rm{mol}}}^{-1})$$
$${{\rm{B}}}_{{\rm{3}}}{{\rm{N}}}_{{\rm{3}}}{{\rm{H}}}_{{\rm{6}}({\rm{g}})}\to 3{{\rm{BN}}}_{({\rm{s}})}+3{{\rm{H}}}_{{\rm{2}}({\rm{g}})}$$
(6)
$$\Delta {{\rm{G}}}^{{\rm{\theta }}}=-\,275.26-0.18{\rm{T}}\,({\rm{KJ}}\cdot {{\rm{mol}}}^{-1})$$
Figure 10
figure 10

TG-DTA curves of raw materials heated to 1100 °C under nitrogen: (a) With salt; (b) Without salt.

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Figure 10b shows the TG-DTA curves of the raw materials heated to 1100 °C without adding salt. The quality change in the sample presents in two distinct phases. In the first stage, the temperature range is approximately 200–300 °C and the corresponding mass loss is 64%. In the second stage, the temperature range is 500–700 °C, corresponding to an 8% mass loss. In addition, there is a slight weight loss at 800–900 °C, corresponding to a 2% mass loss. The total weight loss is 74%. Compared with Fig. 10a, the weight loss is quite large, which means that the synthesis of BN using the MSS method can effectively reduce the loss of raw materials during the reaction process.

The reaction mechanism for forming BN was analyzed in conjunction with Fig. 10. A possible formation process for r-BN is shown in Fig. 11. At approximately 200–300 °C, NH4Cl is partially volatilized or decomposed into NH3. When the temperature is heated to 350 °C, the KBH4 begins to melt. Because KBH4 is easily decomposed by inorganic acid (e.g., HCl), under the pressure generated by the NH3 gas, the KBH4 begins to decompose around 580 °C to produce BH3. When the heating temperature rises to 657 °C, which is the eutectic melting temperature of NaCl-KCl, the liquid phase environment generated by the molten salt envelopes and penetrates the raw material, preventing the transitional volatilization of NH4Cl and slowing down the reaction rate to reduce the loss of generated NH3 and BH3 with nitrogen. NH3 and BH3 are further reacted to form gaseous B3N3H6 intermediates, and this is followed by the slow dehydrogenation of B3N3H6 to produce BN nanoparticles. Finally, the BN nanoparticles aggregate into nuclei and grow into flake-like structures along the BN nuclei. The products were washed several times with distilled water to obtain the final product of BN nanoflakes.

Figure 11
figure 11

Schematic diagram of the r-BN synthesis by molten salt method.

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Antioxidant analysis of r-BN

Studying the antioxidant properties of substances is usually by means of a differential thermal analyzer or the establishment of oxidation kinetics models. In this work, to understand the oxidation resistance of the synthesized BN nanoflakes, the as-prepared BN was subjected to TG and DTA tests. Figure 12 shows the TG-DTA curves of the as-prepared r-BN nanoflakes in air. The TG-DTA curves of the r-BN synthesized at 1100 °C in NaCl-KCl eutectic salts are shown in Fig. 12a. There is an endothermic peak at 80 °C, and the mass loss was due to the volatilization of water molecules in the sample. In addition, a pronounced exothermic peak appears at 1009 °C, which starts at 894 °C and ends at 1084 °C, and the mass of the sample increases and begins to oxidize at 894 °C. Compared with the r-BN triangular nanoplates prepared by Bao et al. (BN started to oxidize at 800 °C)28, the oxidation resistance increased by approximately 100 °C. This result indicates that the as-prepared BN has excellent oxidation resistance and has good application prospects for high-temperature environments. In addition, when the heating temperature is 800–1200 °C, the BN is oxidized to B2O3 with an increase of approximately 37% in mass. Theoretically, BN is oxidized to B2O3 with an increase of approximately 40% in mass, indicating that part of the synthesized BN was not oxidized.

Figure 12
figure 12

TG-DTA curves of the as-prepared BN nanoflakes in air: (a) With salt; (b) Without salt.

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Figure 12b shows the TG-DTA curves of the r-BN synthesized at 1100 °C without adding salt. When the temperature is lower than 600 °C, the sample quality decreases as the heating temperature increased. Furthermore, an exothermic peak appears at 1025 °C, which starts at 901 °C and ends at 1085 °C. When the heating temperature is 800–1200 °C, the BN is oxidized to B2O3 with an increase of approximately 30% in mass. Compared with the synthesis of BN by MSS, this indirectly shows that the BN particles synthesized without the addition of salt were larger. Moreover, this can be confirmed by Figs 3d and 4d.

Conclusions

This study shows that the use of the MSS made it easier to synthesize high-purity r-BN nanoflakes with good morphology in a nitrogen atmosphere at low temperatures. KBH4 and NH4Cl were used as the main raw materials. The effect of salt addition and non-addition on the formation of r-BN was compared, and the heating temperature was also an important factor in the synthesis. High-purity r-BN was synthesized at 650 °C by using the MSS. However, with no salt added, r-BN was synthesized at 900 °C. As the heating temperature increased to 1000 °C, compared with the r-BN synthesized without salt, the r-BN synthesized using the molten NaCl-KCl salt had a uniform morphology. The grain diameter was 200–300 nm and the thickness was 40–70 nm. In addition, at 900–1100 °C, the specific surface area of BN synthesized by the MSS at 1000 °C was the largest, at 294.26 m2/g. Furthermore, the BN prepared at 1100 °C had good oxidation resistance in air, and its elastic modulus value was approximately 1.60 GPa.