Microwave Dielectric Properties of (1-x) Li2MoO4–xMg2SiO4 Composite Ceramics Fabricated by Cold Sintering Process

Introduction

Microwave (MW) dielectric ceramics are a type of multifunctional material widely used for many basic components in communication systems, such as dielectric antenna, oscillators, substrates, and phase shifters (Cava, 2001; Reaney and Iddles, 2006; Zhou et al., 2018). With the rapid development of the fifth generation mobile cellular network (5G) and the requirements of new MW devices, it is necessary to explore novel dielectric materials in order to have fast signal response performance (Fiedziuszko et al., 2002; Ohsato, 2012; Sebastian et al., 2015; Faouri et al., 2019). MW ceramics with low permittivity (ε_r) and low energy loss are extensively used with microwave and millimeterwave (30–300 GHz) radio frequencies as circuit substrates and other functional dielectrics, due to their low signal transmission time delay (Sebastian, 2008). It is well-known that most MW ceramics are prepared by using high temperature solid-state sintering at temperatures greater than 1,200°C. Recently, the fabrication of microwave devices using low-temperature and ultra-low-temperature co-fired ceramic (LTCC and ULTCC) technology has attracted attention because it can make microwave ceramics compatible with sustainable and inexpensive electrodes, such as Ag, Cu, and Al, and meet the requirements of miniaturization, reliability, and low loss of microwave devices. However, there are still lots of problems between LTCC/ULTCC and electrodes, including the formation of parasitic phases by reaction, interdiffusion, and delamination, which is mainly due to their differences in thermal stability, shrinkage rates, and chemical incompatibilities (Green et al., 2008).

Cold sintering process (CSP) has recently been proposed as a method to produce different kinds of dense ceramics and composites under the condition of uniaxial pressure-assisted sintering (100–500 MPa) with low temperatures (<300°C) and short time periods ( ≤1 h), via utilizing water as a transient solvent (Kahari et al., 2014; Kähäri et al., 2016; Guo et al., 2016a,b, 2017; Induja and Sebastian, 2017; Randall et al., 2017; Väätäjä et al., 2017, 2018; Wang et al., 2018, 2019b). Kahari et al. directly pressed Li₂MoO₄ powder at room temperature with an appropriate amount of deionized water. The relative density and microwave dielectric properties of the cold-sintered sample was the same as that of a sample sintered at 540°C (Saraiva et al., 2017). Similarly, other molybdate ceramics such as K₂Mo₂O₇ (Guo et al., 2017), (Bi_0.95Li_0.05)(V_0.9Mo_0.1)O₄-Na₂Mo₂O₇ (Wang et al., 2019a), (LiBi)_0.5MoO₄ (Guo et al., 2017) etc. have been prepared by CSP with acceptable MW dielectric properties and a dense microstructure. Other than the low temperature, the key processing advantages of CSP are that it produces a near shape, that the prepared dense ceramic possesses the same diameter as the model, and that no reaction occurs between different ingredients. Randall et al. reported the fabrication and electrochemical properties of ceramic–salt composite electrolytes from cold sintering (Lee et al., 2019). Reaney et al. addressed cold sintered C0G mulitlayer ceramic capacitors with Ag internal electrodes (Wang et al., 2019b).

On the other hand, silicate ceramics are widely investigated as important low dielectric constant microwave and millimeterwave dielectrics. Pure Mg₂SiO₄ was reported to have a low permittivity (ε_r) of 6.8 and a high Q × f of 240,000 GHz (Tsunooka et al., 2003). Lai et al. reported a good temperature stability and a high Q × f of 237,400 GHz for low temperature (850–950°C) fired Mg₂SiO₄-Li₂TiO₃ composite ceramics (Lai et al., 2017). Zhang et al. reported that a high Q × f of 99,800 GHz for forsterite (Mg_1−xNi_x)₂SiO₄ ceramics at a middle sintering temperature of 1,150°C (Zhang et al., 2014). To our knowledge, there are no reports on cold-sintered silicate ceramics or composites, which might exhibit promising features for 5G enabled technology.

In this work, Li₂MoO₄ and Mg₂SiO₄ were selected to fabricate (1-x) Li₂MoO₄–xMg₂SiO₄ composite ceramics (LMO-xMSO, x = 0, 5, 10, 15, 20, 30, 50, and 90 wt%) by CSP to show the possibility of fabricating dense silicate composite ceramics at a low temperature (≤200°C). The effects of MSO concentration on the microstructure and vibrational lattice modes, as well as microwave dielectric properties, were systematically discussed.

Experimental Section

MSO ceramic powders were prepared via a conventional solid-state sintering method using high purity powders MgO (Acros Organics, 99.99%) and SiO₂ (Acros Organics, 99.99%) as raw materials. Raw materials were weighed according to the nominal stoichiometric compositions, mixed with isopropanol, and ball-milled for 4 h in a planetary ball mill. Then the mixture was dried and calcined at 1,250°C for 4 h in air to synthesize the MSO samples. To prepare LMO-xMSO (x = 5, 10, 20, 30, 50, and 90 wt%) composite ceramics, the prepared MSO and commercially available LMO (Alfa Aesar, 99+%) powders were weighed by weight ratio and mixed with 10–15 wt% deionized water. The wet powders were uniaxially heated at 200°C for 60 min at a pressure of 500 Mpa. The pressed samples were dried in an oven at 120°C for 24 h.

The bulk densities of ceramic pellets were calculated by the geometric method. The room temperature phase combinations were identified by XRD (D2 Phaser, Bruker) using CuKα radiation. The Raman spectroscopy at room temperature was obtained using an in_Via Raman microscope with a green 514.5 nm laser (Renishaw). The microstructures of LMO-xMSO composite ceramics were characterized by a scanning electron microscope (SEM, Inspect F50, FEI) equipped with an energy dispersive spectrometer (EDS). The ε_r and Q × f value were identified by the TE_01δ dielectric resonator method using a R3767CH, Advantest Corporation (Tokyo, Japan) vector network analyzer.

Results and Discussion

Figure 1A presents the relative density (ρr) of LMO-xMSO composite ceramic samples. A high relative density of 85–100% was obtained in LMO-xMSO composite ceramics with x < 50%, which fully demonstrates that dense LMO-xMSO samples can be produced by cold-sintering with the assistance of deionized water where LMO is predominant. Figure 1B shows the XRD patterns at room temperature of LMO-xMSO composite samples with 2θ of 10°-50°. MSO has an island structure (space group Pbnm, JCPDS No.78#1372). LMO has a triangular structure (space group R3, JCPDS No.12#0763) with tetrahedral coordination that was formed by a separate MoO₄ tetrahedron (Barinova et al., 2014; Saraiva et al., 2017). It is clear that two sets of diffraction peaks co-exist without impurities found, corresponding to LMO and MSO phases, respectively, indicating that there are no chemical reactions happening between MSO and LMO.

FIGURE 1

Figure 1. (A) Relative densities and (B) XRD patterns of (1-x) LMO-xMSO composite ceramics.

SEM images of cold-sintered LMO-xMSO composite ceramics are given in Figures 2a–g. The SEM images reveal dense microstructures. It can be clearly observed that there are two discrete phases present in all composite ceramic samples, with the smaller MSO grains surrounding larger LMO grains, in agreement with the X-ray results (Figure 1B). According to the morphology feature and EDS analysis (Figures 2h-l), the large and small grains are LMO and MSO grains, respectively.

FIGURE 2

Figure 2. SEM images of cold-sintered (a) LMO; (b) 95 wt% LMO−5 wt% MSO; (c) 90 wt% LMO−10 wt% MSO; (d) 80 wt% LMO−20 wt% MSO; (e) 70 wt% LMO−30 wt% MSO; (f) 50 wt% LMO−50 wt% MSO and (g) 10 wt% LMO−90 wt% MSO composite ceramics; EDS element mapping of LMO-MSO: (h) element layered image; (i) Mo; (j) Si; (k) O and (l) Mg.

Figure 3 shows the Raman spectra of LMO-xMSO composites at room-temperature ranging from 50 to 1,200 cm⁻¹. According to group theory and irreducible representations, LMO and MSO have 82 and 84 different vibration modes, respectively, as described below:

$\begin{array}{ll}{\Gamma }_{\text{LMO}}=21{\text{A}}_{\text{g}}+20{\text{A}}_{\text{u}}+21{\text{E}}_{\text{g}}+20{\text{E}}_{\text{u}}& (1)\end{array}$

$\begin{array}{ll}{\Gamma }_{\text{MSO}}=11{\text{A}}_{\text{g}}+25{\text{B}}_{\text{g}}+10{\text{A}}_{\text{u}}+38{\text{B}}_{\text{u}}& (2)\end{array}$

For both LMO and MSO, the corresponding Raman active modes are described as 42 (21A_g + 21E_g) and 36 (11A_g + 25B_g), respectively. The E_u and B_u of LMO and MSO are infrared active. Generally, vibrations can be divided into internal and external modes (Barinova et al., 2014; Saraiva et al., 2017). For LMO, the vibrations of the MoO₄ tetrahedron trigger the internal modes, and the movement of Li⁺ cations and the vibrational/translations of the [MoO₄] tetrahedron are related to the external modes (Porto and Scott, 1967; Guo et al., 2014). The Raman bands of LMO are roughly divided into three parts: the bands below 85 cm⁻¹ are due to the translational motions of external modes, most of the bands between 85 and 800 cm⁻¹ belong to a mixture of external and internal modes, and the bands above 800 cm⁻¹ are assigned to the stretching (ν₁ and ν₃) of internal modes. MSO has the crystal structure of forsterite, the binding force of Si-O bonds between atoms inside the silicon tetrahedron is stronger than that between Mg and silicon tetrahedron, and the two strongest Raman bands 824.6 cm⁻¹ and 856.7 cm⁻¹ are assigned to the symmetrical stretching vibration modes (ν₁) of the silicon tetrahedron and the antisymmetric stretching vibration modes (ν₃). The bands above 800 cm⁻¹ are related to the S (Si-O) stretching modes. 400–700 cm⁻¹ is dominated by the Si-O vibration modes. According to the internal modes and the external modes, the bands above 430 cm⁻¹ are assigned to the stretching motions (ν₁ and ν₃) and the bending motions (ν₂ and ν₄) of the internal modes. The bands below 430 cm⁻¹ are related to external modes and are divided into rotational modes (B_g close to 370 cm⁻¹) and translational modes. As the amount of MSO content decreases, the strength of LMO Raman bands peak increases gradually, and the Raman bands of LMO (Ag ~ 68 cm⁻¹, ν₁ ~ 819 cm⁻¹ and ν₁ / ν₃ ~ 902 cm⁻¹) are distinctly diaplayed in all LMO-xMSO composites. The Raman spectra of LMO-xMSO composite ceramics are composed of a superposition of the spectral characteristics of LMO and MSO phases, and the coexistence of LMO and MSO in composites is further confirmed.

FIGURE 3

Figure 3. Raman spectra of (1-x) LMO-xMSO composite ceramics.

The relative permittivity (ε_r) and quality factor (Q × f value) of LMO-xMSO composite ceramics with different MSO weight fractions and a series comparative experimental date are listed in Table 1. It can be seen from Table 1 that cold-sintered pure LMO ceramics at 120°C, 400 MPa for 30 min, exhibit a relative density of 97.4%, ε_r ~ 5.3, and Q × f ~ 24,320 GHz, which is equivalent to those fabricated by the conventional sintering method. As the MSO fraction increases, both ε_r and Q × f are found to decrease from 5.3 and 24,320 to 5.05 and 9,450 GHz, respectively. The τ_f value of LMO-xMSO is in the range of −161 to −118, and does not greatly improve the τ_f compared to LMO.

TABLE 1

Table 1. Sintering temperatures, densities, and microwave dielectric properties of LMO-xMSO composite ceramics.

Conclusions

In this work, novel LMO-xMSO microwave composite ceramics with high relative densities of > 80% were successfully prepared by CSP (200°C, 60 min, and 500 MPa). Two characteristic phases of LMO and MSO were found in all composite ceramics. The result of XRD, SEM, and Raman spectroscopy indicated that there was no chemical reaction between the two phases. With the increase of the MSO weight fraction ε_r decreased from 5.3 to 5.05, and the Q × f value decreased from 24,320 to 9,450 GHz. The successful preparation of (1-x) LMO-xMSO composite ceramics indicates that CSP has great potential in the low temperature fabrication of microwave composite ceramics for 5G enabled technology.

Data Availability Statement

All datasets generated for this study are included in the manuscript/supplementary files.

Author Contributions

All authors listed have made a substantial, direct and intellectual contribution to the work, and approved it for publication.

Funding

This work was supported by the National Natural Science Foundation of China under grant number 51672063 and 51802062, and Open projects of Key Laboratory of inorganic functional materials and devices, Shanghai silicate institutes (KLIFMD201708).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

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