A Novel Method of Si and Si3N4 Powder Resources Recycling: Cold Bonding Briquettes

Silicon nitride (Si3N4) and silicon powder (Si) are two kinds of harmful solid waste in industrial production. As an environmental and low-consumption method, the cold-bonding technique is a novel method to utilize the problem of powder resource cycling. In this experiment, mechanical and high-temperature properties of Si and Si3N4 briquettes were studied after cold bonding. The results are as follows: (1) The compressive strength of the Si and Si3N4 briquettes increased with the improvement of molding pressure. With the same binder (1 wt.%) and water (10 wt.%) addition, the compressive strength of the Si3N4 briquette arrived at 12,023.53 N under 40 Mpa molding pressure, which is much higher than that of the Si briquette (942.40 N). The Si particles are uneven and irregular, which leads to an intense arch bridge effect in the Si briquette and the compressive strength decrease. Compared with Si powder, the particle size and shape of Si3N4 is small, uniform, and regular. The influence of the arch bridge effect is smaller than that in the Si briquette. (2) After being treated at 1473 K for 1 h, the compressive strength of the Si briquette increased to 5049.83 N, and the compressive strength of the Si3N4 briquette had a slight change. The surface of the briquettes was contacted with oxygen and reacted to form an outer shell which mainly contains SiO2 in the high-temperature treatment. FT-IR results have shown there were no extra impurities in cold-bonded briquettes when using the organic binder. (3) The microstructure of the cross section of the Si and Si3N4 briquettes after high-temperature treatment presented that oxygen entered the briquette through the pores and continued to react with the Si and Si3N4. The outer shell of the Si briquette grew and thickened continuously with the oxygen spreading in the Si briquette. However, because of the smaller particle size and regular shape, little oxygen diffused in the Si3N4 briquette. The outer shell of the Si3N4 briquette is fairly thin, so the compressive strength did not change too much.


Introduction
As a high-quality material, silicon nitride (Si 3 N 4 ) is finding applications in ceramics, metallurgy, aircraft, and other industries due to its high-temperature stability, thermal shock resistance, hardness, and wear resistance [1][2][3]. In a reactor, industrial silicon powder is usually used as a raw material to produce Si 3 N 4 with nitrogen gas through the reaction 3Si(s) + 2N 2 (g) = Si 3 N 4 (s) [4,5]. Compared with industrial silicon powder, silicon nitride has preferable chemical stability and physical properties in applications [2]. However, in the production methods [6][7][8][9] of silicon nitride materials, Si 3 N 4 powder is generated as a by-product by crushing the lump. Meanwhile, the application of industrial silicon powder, such as the production of Si-Fe alloys [10][11][12] by using a submerged arc furnace, has a considerable powder emission with off-gas. Both Si and Si 3 N 4 powders collected from industry production are hardly utilized due to the impurity and small particle size.  Figure 1 is the schematic of the cold-bonding molding process. Si or Si 3 N 4 powders (1 kg), water (0.1 kg), and an organic binder (0.01 kg) were mixed sufficiently into a wet mixture at first. Then the wet mixtures were filled into a cylindrical mold and molded into a wet cylindrical briquette under different pressures (5,10,20,30,40 Mpa). Finally, the wet briquettes were dried in a muffle furnace at 180 • C for 12 h in the atmosphere. After the briquettes cooled down to room temperature, the compressive strength of the Si and Si 3 N 4 briquettes was tested on a universal testing machine. The remainder was heated at 1473 K for 1 h in a muffle furnace, and the compressive strength was tested.

Cold Bonding Briquettes Process
Materials 2022, 15, x FOR PEER REVIEW 3 of briquettes were dried in a muffle furnace at 180 °C for 12 h in the atmosphere. After t briquettes cooled down to room temperature, the compressive strength of the Si and Si3 briquettes was tested on a universal testing machine. The remainder was heated at 14 K for 1 h in a muffle furnace, and the compressive strength was tested.

Analysis Method
In this study, the compressive strength was measured on a universal testing machi (UTM, C45.305, MTS, Eden Prairie, MN, USA). X-ray fluorescence spectrometer (XR 1800, Shimadzu, Japan) was used to test the content of the main elements in the powde Phase composition of powders was performed on an X-ray diffractometer (Bruker D8 A vance, Bruker, Germany) with a scan step of 10 (°)/min, in the 2θ range from 5° to 90°. T microstructure and elementals distribution were analyzed by using a scanning electr microscopy with an energy dispersive X-ray spectrometer (Hitachi SU-1500, Hitachi, pan). The briquette was measured on a Fourier transform infrared spectrometer (Therm Scientific Nicolet iS20, Thermo Fisher Scientific, Waltham, MA, USA) using the KBr d technique, and the spectra were measured with a resolution of 4 cm−1 between a wa number range of 4000 to 400 cm −1 .

Effect of Molding Pressure on Compressive Strength of Cold-Bonded Briquette
The compressive strength of different briquettes under various pressures is shown Table 2. The compressive strength of Si and Si3N4 briquettes increases with the moldi pressure augment. Meanwhile, their compressive strength grows significantly after t molding pressure is over 30 Mpa. When the molding pressure arrives at 40 Mpa, the co pressive strength of Si and Si3N4 briquettes are 942.40 N and 12,023.53 N, respective Additionally, the compressive strength of the Si3N4 briquette is dramatically higher th that of the Si briquette under various molding pressures. In the cold-bonding process, particles with inhomogeneous size and irregular sha may cause more pores to form inside of the briquette. This phenomenon is named the ar

Analysis Method
In this study, the compressive strength was measured on a universal testing machine (UTM, C45.305, MTS, Eden Prairie, MN, USA). X-ray fluorescence spectrometer (XRF-1800, Shimadzu, Japan) was used to test the content of the main elements in the powders. Phase composition of powders was performed on an X-ray diffractometer (Bruker D8 Advance, Bruker, Germany) with a scan step of 10 ( • )/min, in the 2θ range from 5 • to 90 • . The microstructure and elementals distribution were analyzed by using a scanning electron microscopy with an energy dispersive X-ray spectrometer (Hitachi SU-1500, Hitachi, Japan). The briquette was measured on a Fourier transform infrared spectrometer (Thermo Scientific Nicolet iS20, Thermo Fisher Scientific, Waltham, MA, USA) using the KBr disc technique, and the spectra were measured with a resolution of 4 cm−1 between a wave number range of 4000 to 400 cm −1 .

Effect of Molding Pressure on Compressive Strength of Cold-Bonded Briquette
The compressive strength of different briquettes under various pressures is shown in Table 2. The compressive strength of Si and Si 3 N 4 briquettes increases with the molding pressure augment. Meanwhile, their compressive strength grows significantly after the molding pressure is over 30 Mpa. When the molding pressure arrives at 40 Mpa, the compressive strength of Si and Si 3 N 4 briquettes are 942.40 N and 12,023.53 N, respectively. Additionally, the compressive strength of the Si 3 N 4 briquette is dramatically higher than that of the Si briquette under various molding pressures. In the cold-bonding process, particles with inhomogeneous size and irregular shape may cause more pores to form inside of the briquette. This phenomenon is named the arch bridge effect [28]. The microstructures of Si and Si 3 N 4 powders are shown in Figure 2a,b, respectively. Compared with the microstructure of Si 3 N 4 powder, the particle sizes and shapes of Si powder are uneven and irregular, which means an intense arch bridge effect in the Si briquette after cold bonding. Thus, the compressive strength of the Si briquette is much lower than that of the Si 3 N 4 briquette.
bridge effect [28]. The microstructures of Si and Si3N4 powders are shown in Figure 2a,b, respectively. Compared with the microstructure of Si3N4 powder, the particle sizes and shapes of Si powder are uneven and irregular, which means an intense arch bridge effect in the Si briquette after cold bonding. Thus, the compressive strength of the Si briquette is much lower than that of the Si3N4 briquette. The compressive-displacement curves of briquettes under different molding pressures are shown in Figure 3a,b, respectively. All of the briquettes have strain-softening characteristics after the compressive strength reaches its maximum. With the molding pressure increasing, pores form due to the decreasing of the arch bridge effect, and the slope of the compressive-strength curves elevates obviously. Matin et al. [29] has studied the process of typical stress versus strain for hard rocks. Similarly, the macroscopic failure process of two briquettes contains four stages: (1) crack closure, (2) elastic region, (3)stable crack growth, and (4) initiation of macro-scale shear failure. At the first stage, the influence of the arch bridge effect reduces gradually, and the slope of the curves increases slowly. When the macroscopic failure process goes to the second stage, the slope elevates to maximum immediately. Meanwhile, the influence of van der Waals force and friction between particles on the compressive strength of the briquettes also increases rapidly. At the third stage, more and more cracks appear inside of briquette, and the slope of compressivestrength curves decreases slightly. Finally, the compressive strength decreases while the slope of curves become negative at the last stage. Furthermore, it can be seen that the compressive-strength curves of Si briquettes are smoother than that of Si3N4 briquettes. That is because the small particle size and regular The compressive-displacement curves of briquettes under different molding pressures are shown in Figure 3a,b, respectively. All of the briquettes have strain-softening characteristics after the compressive strength reaches its maximum. With the molding pressure increasing, pores form due to the decreasing of the arch bridge effect, and the slope of the compressive-strength curves elevates obviously. Matin et al. [29] has studied the process of typical stress versus strain for hard rocks. Similarly, the macroscopic failure process of two briquettes contains four stages: (1) crack closure, (2) elastic region, (3)stable crack growth, and (4) initiation of macro-scale shear failure. At the first stage, the influence of the arch bridge effect reduces gradually, and the slope of the curves increases slowly. When the macroscopic failure process goes to the second stage, the slope elevates to maximum immediately. Meanwhile, the influence of van der Waals force and friction between particles on the compressive strength of the briquettes also increases rapidly. At the third stage, more and more cracks appear inside of briquette, and the slope of compressive-strength curves decreases slightly. Finally, the compressive strength decreases while the slope of curves become negative at the last stage.
bridge effect [28]. The microstructures of Si and Si3N4 powders are shown in Figure 2a,b, respectively. Compared with the microstructure of Si3N4 powder, the particle sizes and shapes of Si powder are uneven and irregular, which means an intense arch bridge effect in the Si briquette after cold bonding. Thus, the compressive strength of the Si briquette is much lower than that of the Si3N4 briquette. The compressive-displacement curves of briquettes under different molding pressures are shown in Figure 3a,b, respectively. All of the briquettes have strain-softening characteristics after the compressive strength reaches its maximum. With the molding pressure increasing, pores form due to the decreasing of the arch bridge effect, and the slope of the compressive-strength curves elevates obviously. Matin et al. [29] has studied the process of typical stress versus strain for hard rocks. Similarly, the macroscopic failure process of two briquettes contains four stages: (1) crack closure, (2) elastic region, (3)stable crack growth, and (4) initiation of macro-scale shear failure. At the first stage, the influence of the arch bridge effect reduces gradually, and the slope of the curves increases slowly. When the macroscopic failure process goes to the second stage, the slope elevates to maximum immediately. Meanwhile, the influence of van der Waals force and friction between particles on the compressive strength of the briquettes also increases rapidly. At the third stage, more and more cracks appear inside of briquette, and the slope of compressivestrength curves decreases slightly. Finally, the compressive strength decreases while the slope of curves become negative at the last stage. Furthermore, it can be seen that the compressive-strength curves of Si briquettes are smoother than that of Si3N4 briquettes. That is because the small particle size and regular Furthermore, it can be seen that the compressive-strength curves of Si briquettes are smoother than that of Si 3 N 4 briquettes. That is because the small particle size and regular shape of Si 3 N 4 powder make the friction between particles greater. Additionally, the excellent mechanical properties of Si 3 N 4 particles [30] also enable the briquette to withstand significant pressure after the arch bridge effect disappears at the second stage.

High-Temperature Properties of Si and Si 3 N 4 Briquettes
In the production of alloy and ceramics, the Si and Si 3 N 4 briquettes are possibly used in high-temperature conditions, respectively. Thus, the briquettes molded under 40 Mpa pressure were treated at 1473 K for 1 h by muffle furnace in air. The cross-sectional photographs of Si and Si 3 N 4 briquettes before and after being treated are shown in Figure 4a,b and Figure 4c,d, respectively. It can be seen from Figure 4a,b clearly that there is a dramatic outer shell that appeared outside of the Si briquette after the high-temperature treatment. As shown in Figure 4c,d, an outer shell is also generated in the high-temperature treatment of the Si 3 N 4 briquette. However, the outer shell of the Si 3 N 4 briquette after treatment is too thin to be seen clearly.
shape of Si3N4 powder make the friction between particles greater. Additionally, the e cellent mechanical properties of Si3N4 particles [30] also enable the briquette to withstan significant pressure after the arch bridge effect disappears at the second stage.

High-Temperature Properties of Si and Si3N4 Briquettes
In the production of alloy and ceramics, the Si and Si3N4 briquettes are possibly us in high-temperature conditions, respectively. Thus, the briquettes molded under 40 M pressure were treated at 1473 K for 1 h by muffle furnace in air. The cross-sectional ph tographs of Si and Si3N4 briquettes before and after being treated are shown in Figure 4a and Figure 4c,d, respectively. It can be seen from Figure 4a,b clearly that there is a dr matic outer shell that appeared outside of the Si briquette after the high-temperature trea ment. As shown in Figure 5c,d, an outer shell is also generated in the high-temperatu treatment of the Si3N4 briquette. However, the outer shell of the Si3N4 briquette after trea ment is too thin to be seen clearly.  Figure 5 indicates the compressive-strength curves of Si and Si3N4 briquettes befo and after being treated at high temperatures. As shown in Figure 5a, the compressiv displacement curves of the Si briquette before and after being treated at 1473 K for 1 were fairly different. On the one hand, the compressive strength of Si briquette enhanc visibly from 942.40 N to 5049.83 N after being treated. On the other hand, the slope of t compressive-strength curve increased significantly in the first three stages of the macr scopic failure process. The fragmentation characteristics of the briquette changed fro strain softening to strain hardening. The first peak of the compressive-strength curve the Si briquette treated appeared at a displacement of the curve at 2.15 mm; then the com pressive strength increased to 5049.83 N.
Compared with the Si briquette, the compressive-strength curve of the Si3N4 b quette after being treated has only slightly changed, as shown in Figure 5b. A minor pe  shape of Si3N4 powder make the friction between particles greater. Additionally, the excellent mechanical properties of Si3N4 particles [30] also enable the briquette to withstand significant pressure after the arch bridge effect disappears at the second stage.

High-Temperature Properties of Si and Si3N4 Briquettes
In the production of alloy and ceramics, the Si and Si3N4 briquettes are possibly used in high-temperature conditions, respectively. Thus, the briquettes molded under 40 Mpa pressure were treated at 1473 K for 1 h by muffle furnace in air. The cross-sectional photographs of Si and Si3N4 briquettes before and after being treated are shown in Figure 4a,b and Figure 4c,d, respectively. It can be seen from Figure 4a,b clearly that there is a dramatic outer shell that appeared outside of the Si briquette after the high-temperature treatment. As shown in Figure 5c,d, an outer shell is also generated in the high-temperature treatment of the Si3N4 briquette. However, the outer shell of the Si3N4 briquette after treatment is too thin to be seen clearly.  Figure 5 indicates the compressive-strength curves of Si and Si3N4 briquettes before and after being treated at high temperatures. As shown in Figure 5a, the compressivedisplacement curves of the Si briquette before and after being treated at 1473 K for 1 h were fairly different. On the one hand, the compressive strength of Si briquette enhanced visibly from 942.40 N to 5049.83 N after being treated. On the other hand, the slope of the compressive-strength curve increased significantly in the first three stages of the macroscopic failure process. The fragmentation characteristics of the briquette changed from strain softening to strain hardening. The first peak of the compressive-strength curve of the Si briquette treated appeared at a displacement of the curve at 2.15 mm; then the compressive strength increased to 5049.83 N.
Compared with the Si briquette, the compressive-strength curve of the Si3N4 briquette after being treated has only slightly changed, as shown in Figure 5b. A minor peak Compared with the Si briquette, the compressive-strength curve of the Si 3 N 4 briquette after being treated has only slightly changed, as shown in Figure 5b. A minor peak appeared at a displacement of the curve at 3 mm, and the compressive strength increased to 12,277.91 N subsequently. The compressive strength of the Si 3 N 4 briquette increased 254.38 N after high-temperature treatment. Meanwhile, the fragmentation characteristics of compressive-strength curves before and after high-temperature treatment were similar. Figure 6a shows the XRD patterns of the Si briquette and the outer shell. The phase composition of the Si briquette is significantly different from the outer shell. The Si briquette mainly consists of Si and FeSi 2 (orthorhombic), and the peaks of SiO 2 and FeSi 2 (tetragonal) appear in the XRD pattern of the outer shell. In the process of high-temperature treatment, Si and O 2 react to form SiO 2 , and FeSi 2 (orthorhombic) transforms to FeSi 2 (tetragonal). Similarly, as Figure 6b shows, the phase compositions of Si 3 N 4 powder are α-Si 3 N 4 , β-Si 3 N 4 , MnSiN 2 , and Fe 0 . 905 Si 0 . 095 . Visibly, the SiO 2 also appears in the outer shell of the Si 3 N 4 briquette. Both XRD patterns indicated that the formation of SiO 2 is the main reason for improving the compressive strength of these two cold-bonded briquettes.
appeared at a displacement of the curve at 3 mm, and the compressive strength increased to 12,277.91 N subsequently. The compressive strength of the Si3N4 briquette increased 254.38 N after high-temperature treatment. Meanwhile, the fragmentation characteristics of compressive-strength curves before and after high-temperature treatment were similar. Figure 6a shows the XRD patterns of the Si briquette and the outer shell. The phase composition of the Si briquette is significantly different from the outer shell. The Si briquette mainly consists of Si and FeSi2 (orthorhombic), and the peaks of SiO2 and FeSi2 (tetragonal) appear in the XRD pattern of the outer shell. In the process of high-temperature treatment, Si and O2 react to form SiO2, and FeSi2 (orthorhombic) transforms to FeSi2 (tetragonal). Similarly, as Figure 6b shows, the phase compositions of Si3N4 powder are α-Si3N4, β-Si3N4, MnSiN2, and Fe0.905Si0.095. Visibly, the SiO2 also appears in the outer shell of the Si3N4 briquette. Both XRD patterns indicated that the formation of SiO2 is the main reason for improving the compressive strength of these two cold-bonded briquettes. In the high-temperature process, both Si powder and Si3N4 powder on the briquette surface react with O2 and generate SiO2 easily as follows reactions (1) and (2): (1) Si3N4 + O2 → SiO2 + NO2 (2) As shown in Figure 7, the SiO2 produced by the above reactions has undergone a process from amorphous to crystalline and makes the surface of briquettes more compact, and the compressive strength of the briquette improves with the growth of the shell thickness. Meanwhile, the growth of the outer shell stops since amorphous SiO2 blocks the pores on the surface of the briquette. Due to the particle sizes and shapes of Si particles being more uneven and irregular than that of Si3N4 particles, the size of pores on the surface of Si briquettes is too large and the O2 diffuses in the briquette more deeply. Thus, the outer shell of the Si briquette is thicker than that of the Si3N4 briquette, which means the compressive strength of the Si briquette improved more after high-temperature treatment. In the high-temperature process, both Si powder and Si 3 N 4 powder on the briquette surface react with O 2 and generate SiO 2 easily as follows reactions (1) and (2): (1) As shown in Figure 7, the SiO 2 produced by the above reactions has undergone a process from amorphous to crystalline and makes the surface of briquettes more compact, and the compressive strength of the briquette improves with the growth of the shell thickness. Meanwhile, the growth of the outer shell stops since amorphous SiO 2 blocks the pores on the surface of the briquette. Due to the particle sizes and shapes of Si particles being more uneven and irregular than that of Si 3 N 4 particles, the size of pores on the surface of Si briquettes is too large and the O 2 diffuses in the briquette more deeply. Thus, the outer shell of the Si briquette is thicker than that of the Si 3 N 4 briquette, which means the compressive strength of the Si briquette improved more after high-temperature treatment.

FT-IR Analysis of Si and Si3N4 Briquettes
Organic binders are usually used in the cold-bonding process. However, the briquette has poor performance in high temperatures when using organic binders [25]. Therefore, it is interesting that the compressive strength of the briquette increased after being treated at 1473 K for 1 h. In this research, FT-IR analysis is used to detect the nature of the functional groups [31] present in the powders, briquettes before being treated, and briquettes after being treated.
The results of FT-IR analysis of Si and Si3N4 (powder, briquette, and outer shell) are

FT-IR Analysis of Si and Si 3 N 4 Briquettes
Organic binders are usually used in the cold-bonding process. However, the briquette has poor performance in high temperatures when using organic binders [25]. Therefore, it is interesting that the compressive strength of the briquette increased after being treated at 1473 K for 1 h. In this research, FT-IR analysis is used to detect the nature of the functional groups [31] present in the powders, briquettes before being treated, and briquettes after being treated.
The results of FT-IR analysis of Si and Si 3 N 4 (powder, briquette, and outer shell) are shown in Figure 8a,b, respectively. As shown in Figure 8a, the result of the Si powder is similar to that of the Si briquette, which indicates that the organic binder has decomposed at 180 • C. The peak at approximately 3417 cm −1 and 1627 cm −1 is attributed to the stretching vibration of O-H of adsorbed water and bending vibrations of the crystal water in Si powder [32]. Meanwhile, the O-H band is also existent in the Si briquette and outer shell because of the adsorption of water molecules [33]. Peaks at 1084.08 cm −1 and 1037.73 cm −1 correspond to the asymmetric stretching vibration of Si-O-Si [34,35], and the appearance of a low-frequency band at 436.51 cm −1 and 437.32 cm −1 is due to Fe stretching vibration [36]. The FT-IR spectra of the outer shell are quite different from that of the Si powder and briquette. In the spectra of the outer shell, two strong bands appeared at 907.00 cm −1 and 960.34 cm −1 because of the asymmetric stretching vibration of Si-O-Si and Si-O [37]. Furthermore, a weak band at 536.78 cm −1 is also due to Fe stretching vibration [38]; the reason for the change of Fe band position is the crystal transition of FeSi 2 .

FT-IR Analysis of Si and Si3N4 Briquettes
Organic binders are usually used in the cold-bonding process. However, the briquette has poor performance in high temperatures when using organic binders [25]. Therefore, it is interesting that the compressive strength of the briquette increased after being treated at 1473 K for 1 h. In this research, FT-IR analysis is used to detect the nature of the functional groups [31] present in the powders, briquettes before being treated, and briquettes after being treated.
The results of FT-IR analysis of Si and Si3N4 (powder, briquette, and outer shell) are shown in Figure 8a,b, respectively. As shown in Figure 8a, the result of the Si powder is similar to that of the Si briquette, which indicates that the organic binder has decomposed at 180 °C . The peak at approximately 3417 cm −1 and 1627 cm −1 is attributed to the stretching vibration of O-H of adsorbed water and bending vibrations of the crystal water in Si powder [32]. Meanwhile, the O-H band is also existent in the Si briquette and outer shell because of the adsorption of water molecules [33]. Peaks at 1084.08 cm −1 and 1037.73 cm −1 correspond to the asymmetric stretching vibration of Si-O-Si [34,35], and the appearance of a low-frequency band at 436.51 cm −1 and 437.32 cm −1 is due to Fe stretching vibration [36]. The FT-IR spectra of the outer shell are quite different from that of the Si powder and briquette. In the spectra of the outer shell, two strong bands appeared at 907.00 cm −1 and 960.34 cm −1 because of the asymmetric stretching vibration of Si-O-Si and Si-O [37]. Furthermore, a weak band at 536.78 cm −1 is also due to Fe stretching vibration [38]; the reason for the change of Fe band position is the crystal transition of FeSi2.   Figure 8a shows that the FT-IR spectra of Si3N4 powder, briquette, and outer shell are similar. The peak at approximately 840 cm −1 in FT-IR spectra of Si3N4 powder, briquette, and the outer shell is mainly attributed to the Si-N bond [39]. Meanwhile, the bands that appeared at approximately 570 cm −1 and 440 cm −1 are characteristic absorption frequencies of the β-Si3N4 [40]. The peak at 490 cm −1 is assigned to the Si-O-Si bending mode owing  Figure 8a shows that the FT-IR spectra of Si 3 N 4 powder, briquette, and outer shell are similar. The peak at approximately 840 cm −1 in FT-IR spectra of Si 3 N 4 powder, briquette, and the outer shell is mainly attributed to the Si-N bond [39]. Meanwhile, the bands that appeared at approximately 570 cm −1 and 440 cm −1 are characteristic absorption frequencies of the β-Si 3 N 4 [40]. The peak at 490 cm −1 is assigned to the Si-O-Si bending mode owing to a small amount of SiO 2 in Si 3 N 4 powder. In the process of desiccation and high-temperature treatment, reaction (2) takes place and more SiO 2 is generated. Thus, the peak appears at 1046.38 cm −1 and 1046.28 cm −1 which is in spectra of the briquette and outer shell, respectively.

Microscopic Morphology of Si and Si 3 N 4 Briquette after High Temperature
The microscopic morphology and EDS image of the cross section of the Si and Si 3 N 4 briquette after high-temperature treatment are presented in Figure 9. Figure 9a is the microscopic morphology of the cross section of the Si briquette. It can be seen clearly that the outer shell is fairly smooth, which means the surface of the Si briquette becomes more compact after high-temperature treatment. Figure 9c is the EDS image of the outer shell, and it can be found that the outer shell mainly consisted of SiO 2 . In the high-temperature treatment, the SiO 2 formed in the outer shell has undergone a process from amorphous to crystalline, which will make the surface more compact. Furthermore, because the pores in the Si briquette are too large to be blocked, oxygen can enter in Si briquette easily. Thus, the outer shell will become thicker and thicker during the high-temperature treatment.
outer shell is fairly smooth, which means the surface of the Si briquette becomes more compact after high-temperature treatment. Figure 9c is the EDS image of the outer shell, and it can be found that the outer shell mainly consisted of SiO2. In the high-temperature treatment, the SiO2 formed in the outer shell has undergone a process from amorphous to crystalline, which will make the surface more compact. Furthermore, because the pores in the Si briquette are too large to be blocked, oxygen can enter in Si briquette easily. Thus, the outer shell will become thicker and thicker during the high-temperature treatment.  Figure 9b shows the microscopic morphology of the cross section of the Si3N4 briquette after high-temperature treatment, and Figure 9d is the EDS image of the outer shell. As Figure 9b shows, the thickness of the outer shell is not uniform, which is unlike that of the Si briquette. Dramatically, the outer shell of the Si3N4 briquette is smoother than that of the Si briquette. In addition, it can also be seen that the outer shell of the Si3N4 briquette mainly consists of SiO2 from the EDS image. Due to the particle size and shape of Si3N4 being small and regular, the formed pores are diminutive during the cold-bonding process, and reaction (2) can make the pores blocked easily. Meanwhile, a smooth outer shell can also prevent oxygen from entering the inside of the Si3N4 briquette during the hightemperature treatment. Lastly, the oxygen can enter inside and continue to react in some  Figure 9b shows the microscopic morphology of the cross section of the Si 3 N 4 briquette after high-temperature treatment, and Figure 9d is the EDS image of the outer shell. As Figure 9b shows, the thickness of the outer shell is not uniform, which is unlike that of the Si briquette. Dramatically, the outer shell of the Si 3 N 4 briquette is smoother than that of the Si briquette. In addition, it can also be seen that the outer shell of the Si 3 N 4 briquette mainly consists of SiO 2 from the EDS image. Due to the particle size and shape of Si 3 N 4 being small and regular, the formed pores are diminutive during the cold-bonding process, and reaction (2) can make the pores blocked easily. Meanwhile, a smooth outer shell can also prevent oxygen from entering the inside of the Si 3 N 4 briquette during the high-temperature treatment. Lastly, the oxygen can enter inside and continue to react in some places with large pores on the surface, and the thickness of the shell is uneven. Although the compressive strength of the Si 3 N 4 briquette does not change much because the outer shell was fairly thin, it still can be seen that a small fracture peak appears in the compressive-strength curve.

Conclusions
In this work, a novel method of Si and Si 3 N 4 powder resources recycling has been proposed. As an environmental and low-consumption method, the Si and Si 3 N 4 powder resources can be effectively reused via the cold-bonding technique. In the present work, the mechanical properties and high-temperature properties of Si and Si 3 N 4 briquettes are studied. The results are as follows: (1) The compressive strength of Si and Si 3 N 4 briquettes increases with the improvement of molding pressure. With the same binder (1 wt.%) and water (10 wt.%) addition, the compressive strength of the Si 3 N 4 briquette arrives at 12023.53 N under 40 Mpa molding pressure, which is much higher than that of the Si briquette (942. 40 N). The microstructure of powders shows that the Si particles have uneven particle sizes and irregular shapes. Thus, an intense arch bridge effect appears in the Si briquette, which leads to a decrease in compressive strength. Compared with Si powder, the particle size and shape of Si 3 N 4 is small and regular, and the influence of the arch bridge effect is smaller than that in the Si briquette. (2) After being treated at 1473 K for 1 h, the compressive strength of the Si briquette increases to 5049.83 N, and the compressive strength of the Si 3 N 4 briquette has a slight change. The surface of briquettes is contacted with oxygen and reacts to form an outer shell in the high-temperature treatment. The XRD patterns indicated that the outer shell of Si and Si 3 N 4 briquettes mainly consist of SiO 2 . FT-IR results have shown there are no extra impurities in cold-bonded briquettes. The organic binder decomposed completely after drying the briquette at 180 • C. (3) The microstructure of the cross section of Si and Si 3 N 4 briquettes after high-temperature treatment presented that oxygen enters the briquette through the pores and continues to react with the Si and Si 3 N 4 . In this process, the outer shell of the Si briquette grows and thickens continuously because the pores in the Si briquette are large enough to spread oxygen, thus the compressive strength improves obviously. The particle size of Si 3 N 4 is small and the shape is regular, there are fewer small pores on the surface, and they are easily blocked in the high-temperature process. Lastly, little oxygen enters in Si 3 N 4 briquette and produces a very thin outer shell, so the compressive strength does not change too much.