# Evaluating the Effects of Chemical Composition on Induction Heating Ability of Fe2O3-CaO-SiO2 Glass Ceramics

Authors: Y. Y. Wang; B. Li; Y. L. Yu; P. S. Tang
Journal: Advances in Materials Science and Engineering
 (2016)

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## Abstract

In order to investigate the relationship between induction heating ability of Fe2O3-CaO-SiO2 glass ceramics and chemical composition, a series of glass ceramic samples with different chemical compositions were prepared by the sol-gel method. The structural, textural, and magnetic properties of the samples were analyzed and correlated with the Fe2O3 content. This is the first time work of its kind that evaluates the relationships between induction heating ability and chemical composition of Fe2O3-CaO-SiO2 glass ceramics. The results showed that induction heating ability of Fe2O3-CaO-SiO2 glass ceramics increased gradually with increasing magnetite content. Also, the induction heating ability became considerably better when a small amount of phosphorus was introduced. This study thus reveals a methodology to control the induction heating ability of Fe2O3-CaO-SiO2 glass ceramics through modifying the chemical composition.


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## Body

## 1. Introduction

Magnetic induction hyperthermia has been found to be a useful modality for cancer therapy recently and the thermoseed materials used in hyperthermia therapy have become a topic of increasing research focus [1–3]. The thermoseed material must be biocompatible and contain a magnetic phase to generate and dissipate the proper amount of heat under alternating magnetic fields. Ferromagnetic and bioactive glass ceramics are considered to be effective thermoseed materials for cancer therapy. In particular, Fe2O3-CaO-SiO2 glass ceramics are of great interest to researchers, due to their excellent magnetic properties and good biological activity. Several Fe2O3-CaO-SiO2 glass ceramics having a considerable amount of magnetic phases have been developed for this application [4–7]. In fact, hyperthermic cancer therapy using Fe2O3-CaO-SiO2 ferromagnetic glass ceramics has already been reported to show excellent results in animal experiment [8–10].Fe2O3-CaO-SiO2 glass ceramics absorb magnetic energy and generate heat under the alternating magnetic field, as a result of eddy currents, Néel losses, and hysteresis losses [11–13]. There are several factors that influence the heat production rate [14], including the internal factors such as permeability, magnetic energy product, material size, and microstructure, as well as external factors such as magnetic field frequency and amplitude. The magnetic property was found to be one of the most significant factors affecting the induction heating ability of glass ceramics. Lee et al. explored the effect of the iron state on crystallization in Fe2O3-CaO-SiO2 glasses [15], while Bretcanu et al. investigated the influence of crystallized Fe3O4 on magnetic properties of ferrimagnetic glass ceramics [16]. Magnetic properties of CaO-P2O5-Na2O-Fe2O3-SiO2 glass upon heat treatment were also analyzed by Shankhwar et al. [17]. However, to date, the effects of chemical compositions on the induction heating ability of Fe2O3-CaO-SiO2 glass ceramics have not been reported.The Fe2O3-CaO-SiO2 glass ceramics with different compositions were prepared by the sol-gel method in this work. A small amount of phosphorus was introduced to increase the biological activity at the same time. Magnetic properties of the glass ceramic samples were evaluated and correlated mainly with the iron oxide content. The effect of Fe2O3 content on the induction heating ability of Fe2O3-CaO-SiO2 glass ceramics has been investigated by analyzing the crystal phase and magnetic properties of the samples. This study also reveals a methodology to control the magnetic properties of Fe2O3-CaO-SiO2 glass ceramics through the chemical composition and its potential application in hyperthermia treatment of cancer.


## 2. Materials and Methods

### 2.1. Preparation of Fe2O3-CaO-SiO2 Glass Ceramics

Several different Fe2O3-CaO-SiO2 glass ceramics samples were prepared by the sol-gel method and classified as groups A1 and A2 (without phosphorous and with phosphorous, resp.).The chemical compositions of the samples are shown in Table1. The dosages of reagents calculated on the base of the chemical compositions were listed in Table 2. Briefly, the procedure involved preparing a solution of tetraethyl orthosilicate (TEOS) in ethanol. Distilled water was added to the solution such that the molar ratio of TEOS and water was 1 : 15. Then hydrochloric acid was added to the solution and stirred with a magnetic stirrer for 10 min, and then calcium nitrate and iron nitrate were added to the solution. Triethyl phosphate was also added to the solution in group A2 at this time. The resulting solution was placed in a water bath at 45°C for 150 min. Then the temperature was raised up to 65°C until the solution became semisolid. The samples were aged for 7 days at room temperature, and the gels obtained were baked in the drying oven at 120°C for 12 h. Finally, the dried samples were heated to 650°C for an hour, followed by further heating at 950°C for 1 hour in a heat treatment furnace in a reducing atmosphere. The glass ceramic samples thus obtained were cooled to room temperature and characterized as described in the following sections.Table 1
Chemical compositions of different glass ceramic samples (wt%).
Sample
Fe2O3
CaO
SiO2
P2O5
A1S1
15
42
43
0
A1S3
20
39
41
0
A1S5
25
36
39
0
A1S7
30
34
36
0
A1S9
35
32
33
0
A2P1
30
39
30
1
A2P7
28
37
28
7Table 2
The amount of the reagent.
Sample
Iron nitrate (g)
Calcium nitrate (g)
TEOS (mL)
Triethyl phosphate (mL)
Ethanol (mL)
A1S1
3.62
8.43
7.60
0
22.80
A1S3
4.82
7.83
7.25
0
21.74
A1S5
6.03
7.22
6.89
0
20.68
A1S7
7.23
6.82
6.36
0
19.09
A1S9
8.44
6.42
5.83
0
17.50
A2P1
7.23
8.03
5.30
0.12
15.91
A2P7
6.75
7.59
4.82
0.76
14.46


### 2.2. Characterization

X-ray diffraction (XRD) analysis was performed with a XD-6 X-ray diffractometer at room temperature, with CuKα radiation, 36 kV voltage, and 20 mA current. X-ray data were collected in the 5
<
2
θ
<
80 range. Prior to the XRD test, the samples were ground into powder and sieved through a 300-mesh gauze.Microarea elemental compositions of the samples were determined using a scanning electron microscopy (SEM) system (S-3400N) equipped with energy dispersive spectrometer (EDS). The samples were coated with a layer of gold approximately 10 nm thick, and the samples were analyzed for a live time of 30 s. The total amounts of oxide in the samples were normalized to 100%, and the Fe2+ and Fe3+ contents were converted to the equivalent Fe2O3 content.Magnetization measurements were performed using a vibrating sample magnetometer (VSM, Lakeshore model 7407) at room temperature.A homemade device was built for measuring the induction heating ability (Figure1). The glass ceramics samples were introduced into a copper coil, which was part of a resonant RLC circuit producing an AC magnetic field in the frequency range 80 kHz–100 kHz and with amplitudes up to 0.15 kA/m. The copper coil was cooled by circulating water, and the temperature was monitored using a fiber thermometer placed in the center of the sample. The induction heating ability was determined by plotting the initial linear rise in temperature versus time, normalized to the mass of the sample.Figure 1
Homemade device for measuring induction heating ability.


## 2.1. Preparation of Fe2O3-CaO-SiO2 Glass Ceramics

Several different Fe2O3-CaO-SiO2 glass ceramics samples were prepared by the sol-gel method and classified as groups A1 and A2 (without phosphorous and with phosphorous, resp.).The chemical compositions of the samples are shown in Table1. The dosages of reagents calculated on the base of the chemical compositions were listed in Table 2. Briefly, the procedure involved preparing a solution of tetraethyl orthosilicate (TEOS) in ethanol. Distilled water was added to the solution such that the molar ratio of TEOS and water was 1 : 15. Then hydrochloric acid was added to the solution and stirred with a magnetic stirrer for 10 min, and then calcium nitrate and iron nitrate were added to the solution. Triethyl phosphate was also added to the solution in group A2 at this time. The resulting solution was placed in a water bath at 45°C for 150 min. Then the temperature was raised up to 65°C until the solution became semisolid. The samples were aged for 7 days at room temperature, and the gels obtained were baked in the drying oven at 120°C for 12 h. Finally, the dried samples were heated to 650°C for an hour, followed by further heating at 950°C for 1 hour in a heat treatment furnace in a reducing atmosphere. The glass ceramic samples thus obtained were cooled to room temperature and characterized as described in the following sections.Table 1
Chemical compositions of different glass ceramic samples (wt%).
Sample
Fe2O3
CaO
SiO2
P2O5
A1S1
15
42
43
0
A1S3
20
39
41
0
A1S5
25
36
39
0
A1S7
30
34
36
0
A1S9
35
32
33
0
A2P1
30
39
30
1
A2P7
28
37
28
7Table 2
The amount of the reagent.
Sample
Iron nitrate (g)
Calcium nitrate (g)
TEOS (mL)
Triethyl phosphate (mL)
Ethanol (mL)
A1S1
3.62
8.43
7.60
0
22.80
A1S3
4.82
7.83
7.25
0
21.74
A1S5
6.03
7.22
6.89
0
20.68
A1S7
7.23
6.82
6.36
0
19.09
A1S9
8.44
6.42
5.83
0
17.50
A2P1
7.23
8.03
5.30
0.12
15.91
A2P7
6.75
7.59
4.82
0.76
14.46


## 2.2. Characterization

X-ray diffraction (XRD) analysis was performed with a XD-6 X-ray diffractometer at room temperature, with CuKα radiation, 36 kV voltage, and 20 mA current. X-ray data were collected in the 5
<
2
θ
<
80 range. Prior to the XRD test, the samples were ground into powder and sieved through a 300-mesh gauze.Microarea elemental compositions of the samples were determined using a scanning electron microscopy (SEM) system (S-3400N) equipped with energy dispersive spectrometer (EDS). The samples were coated with a layer of gold approximately 10 nm thick, and the samples were analyzed for a live time of 30 s. The total amounts of oxide in the samples were normalized to 100%, and the Fe2+ and Fe3+ contents were converted to the equivalent Fe2O3 content.Magnetization measurements were performed using a vibrating sample magnetometer (VSM, Lakeshore model 7407) at room temperature.A homemade device was built for measuring the induction heating ability (Figure1). The glass ceramics samples were introduced into a copper coil, which was part of a resonant RLC circuit producing an AC magnetic field in the frequency range 80 kHz–100 kHz and with amplitudes up to 0.15 kA/m. The copper coil was cooled by circulating water, and the temperature was monitored using a fiber thermometer placed in the center of the sample. The induction heating ability was determined by plotting the initial linear rise in temperature versus time, normalized to the mass of the sample.Figure 1
Homemade device for measuring induction heating ability.


## 3. Results and Discussion

### 3.1. Crystal Phase Analysis

XRD patterns of the glass ceramic samples of group A1 are shown in Figure2(a), demonstrating the presence of a mixture of crystalline phases for all the materials. Three major crystalline phases, wollastonite (JCPDS No. 84-0654), magnetite (JCPDS No. 85-1436), and hematite (JCPDS No. 85-0599) were observed in group A1 samples. The hematite level of sample A1S9 was much higher than those of other samples. XRD patterns of the glass ceramic samples of group A2 with phosphorus were characterized by the major hydroxyapatite phase (JCPDS No. 09-0432) in addition to the above three major crystalline phases (Figure 2(b)). Hydroxyapatite is the main constituent of bones, and the presence of this bone mineral phase along with the magnetic phase suggests both the biocompatible nature and the induction heating ability of the samples.Figure 2
Room temperature XRD patterns of glass ceramic samples.
(a)
(b)The relative mass of each phase, which was also calculated according to the XRD patterns, was listed in Table3. The amounts of both magnetite and hematite phase of group A2 were more than that of group A1, and the increase of magnetite content indicates that the induction heating ability would get stronger.Table 3
The relative mass of the phases of the samples (wt%).
Sample
Hematite
Magnetite
Wollastonite
Hydroxyapatite
A1S1
4.7
2.8
92.5
0
A1S3
2.5
2.6
94.8
0
A1S5
2.4
1.6
96.1
0
A1S7
3.8
4.8
91.4
0
A1S9
5.9
4.2
89.9
0
A2P1
15
6
45.1
33.9
A2P7
7.5
4.5
50
38


### 3.2. Chemical Composition Analysis

The SEM-EDS spectra for the samples are shown in Figure3. The results confirmed the presence of silicon, calcium, and iron in samples A1S5 and A1S7 while silicon, phosphorus, calcium, and iron were present in all the samples of group A2. Samples A1S5 and A1S7 showed the presence of lathlike particles while the mineral particles in group A2 were granular. Moreover, the particle sizes of A2P1 were about 3 μm, which was much smaller than that of A1S7 which was about 16 μm. The chemical compositions of the samples calculated from EDS are given in Table 4. No other elements were identified, which ruled out the influence of impurities on the induction heating ability of the samples.Table 4
Chemical composition of the samples determined by SEM-EDS (wt%).
Fe2O3
CaO
SiO2
P2O5
A1S5
28.71
37.75
33.54
0
A1S7
22.73
32.79
45.01
0
A2P1
32.57
34.26
30.40
2.76
A2P7
32.05
30.95
25.31
11.70Figure 3
SEM-EDS spectra and images of the samples.


### 3.3. Magnetic Properties

Figure4 shows the magnetization (M
-
H) curves obtained for the samples as a function of applied magnetic field. The samples exhibit hysteresis with narrow hysteresis loop and low coercivity, suggesting the soft ferromagnetic nature of the samples. This is due to the formation of the magnetic phase upon heat treatment, as already confirmed by the XRD results.Figure 4
M
-
H curves of the glass ceramic samples with different chemical composition.The different magnetic parameters of the samples are listed in Table5. Sample A1S7 shows higher saturation magnetization M
s (19 emu/g) and remanent magnetization M
r (2.3 emu/g) than the other samples of group A1. This may be due to the enhancement in the magnetic phase in A1S7. However, M
s and M
r values began to decrease when the Fe2O3 content was over 30% (Figure 5), which can be attributed to the higher hematite content and the lower magnetite content. A2P1 has a lower saturation magnetization value but a larger coercive force compared to A1S7. The lower saturation magnetization may be attributed to some possible reactions during the heating process. It is a known fact that P2O5 and SiO2 can easily react with Fe2O3 forming nonmagnetic phases at high temperature [18]. Also, Fe could enter into the crystalline structure forming a solid solution [19]. The coercive field was also influenced in a significant way by the crystal dimensions [20]. The SEM results showed that the average crystallite size of A2P1 was smaller than that of A1S7. The smaller crystallite size of the magnetic phase results in a larger coercive force. These observed phenomena were similar to previous reports [21].Table 5
Magnetic parameters of the samples.
A1S1
A1S3
A1S5
A1S7
A1S9
A2P1
A2P7
H
c (G)
147.76
124.82
206.83
106.24
82.45
113.85
87.87
M
s (emu/g)
1.99
2.06
3.32
19
17.09
10.99
10.65
M
s
∗ (emu/g)
13.27
10.30
13.28
63.33
48.83
36.63
38.04
M
r (emu/g)
0.33
0.41
0.60
2.30
0.78
2.25
3.04
Interpolated hysteresis area
65649
176034
287151
1683193
525486
923229
980057
Note:M
s values were normalized to the total weight of the sample; M
s
∗ values were normalized to the weight of Fe2O3 component alone.Figure 5
Relationship between magnetic properties and the Fe2O3 content.Figure5 shows the relationship between the different magnetic parameters and Fe2O3 content of the samples. The integrated hysteresis loop area was calculated for a maximum applied field of 10000 G. The relationship between integrated loop area and the Fe2O3 content was similar to that observed in the case of saturation magnetization. It can be seen from Figure 5 that the hysteresis loop area of A1S7 with 30% Fe2O3 content is much larger than that of the other samples in group A1, which may be attributed to the higher remanence of A1S7. Theoretically, the energy generated by the glass ceramic samples under low magnetic field can be estimated from the hysteresis loop area [6]. Thus, the above results indicate that A1S7 should be capable of generating a larger amount of heat than the other samples, under a proper alternating magnetic field.


### 3.4. Induction Heating Ability

To test the heating ability of the samples, the induction heating experiments were performed with the different samples. Hyperthermia heating curves, measured at a fixed current of 2 A for 11 min with 1 g concentrations of the samples, are shown in Figure6. The heating rates of the samples were basically the same, and the temperature increased rapidly until 10 min. The temperature variation amplitudes of the samples were found to increase gradually with the increase of Fe2O3 content of the samples. However, the induction heating ability began to fall when the Fe2O3 content was over 30%, which may be caused by the lower magnetite content. Sample A1S7 showed the largest temperature variation amplitudes of 2.7°C in group A1, which is consistent with the results in previous sections. More interestingly, the temperature variation amplitudes of all the samples in group A1 were about 2°C, while the temperature variation amplitudes of the samples in group A2 with phosphorus were as high as 15°C. The addition of phosphorus not only changed the crystalline phase of the samples but also significantly increased their induction heating ability. These results indicate that P2O5-Fe2O3-CaO-SiO2 glass ceramics are more suitable for hyperthermia treatment than Fe2O3-CaO-SiO2 glass ceramics.Figure 6
Temperature evolution as a function of time in the hyperthermia tests.In ferromagnetic materials, heat generation is mainly due to hysteresis loss. In addition, other physical parameters such as particle size and distribution of the components, as well as magnetic field intensity, also considerably influence the heating properties under AC magnetic field. The effect of these factors may be the reason for the ability of group A2 samples to generate more heat than group A1 samples. Further work is in progress in our laboratory to understand the heating properties of this class of glass ceramics and to optimize the composition for therapeutic application.


## 3.1. Crystal Phase Analysis

XRD patterns of the glass ceramic samples of group A1 are shown in Figure2(a), demonstrating the presence of a mixture of crystalline phases for all the materials. Three major crystalline phases, wollastonite (JCPDS No. 84-0654), magnetite (JCPDS No. 85-1436), and hematite (JCPDS No. 85-0599) were observed in group A1 samples. The hematite level of sample A1S9 was much higher than those of other samples. XRD patterns of the glass ceramic samples of group A2 with phosphorus were characterized by the major hydroxyapatite phase (JCPDS No. 09-0432) in addition to the above three major crystalline phases (Figure 2(b)). Hydroxyapatite is the main constituent of bones, and the presence of this bone mineral phase along with the magnetic phase suggests both the biocompatible nature and the induction heating ability of the samples.Figure 2
Room temperature XRD patterns of glass ceramic samples.
(a)
(b)The relative mass of each phase, which was also calculated according to the XRD patterns, was listed in Table3. The amounts of both magnetite and hematite phase of group A2 were more than that of group A1, and the increase of magnetite content indicates that the induction heating ability would get stronger.Table 3
The relative mass of the phases of the samples (wt%).
Sample
Hematite
Magnetite
Wollastonite
Hydroxyapatite
A1S1
4.7
2.8
92.5
0
A1S3
2.5
2.6
94.8
0
A1S5
2.4
1.6
96.1
0
A1S7
3.8
4.8
91.4
0
A1S9
5.9
4.2
89.9
0
A2P1
15
6
45.1
33.9
A2P7
7.5
4.5
50
38


## 3.2. Chemical Composition Analysis

The SEM-EDS spectra for the samples are shown in Figure3. The results confirmed the presence of silicon, calcium, and iron in samples A1S5 and A1S7 while silicon, phosphorus, calcium, and iron were present in all the samples of group A2. Samples A1S5 and A1S7 showed the presence of lathlike particles while the mineral particles in group A2 were granular. Moreover, the particle sizes of A2P1 were about 3 μm, which was much smaller than that of A1S7 which was about 16 μm. The chemical compositions of the samples calculated from EDS are given in Table 4. No other elements were identified, which ruled out the influence of impurities on the induction heating ability of the samples.Table 4
Chemical composition of the samples determined by SEM-EDS (wt%).
Fe2O3
CaO
SiO2
P2O5
A1S5
28.71
37.75
33.54
0
A1S7
22.73
32.79
45.01
0
A2P1
32.57
34.26
30.40
2.76
A2P7
32.05
30.95
25.31
11.70Figure 3
SEM-EDS spectra and images of the samples.


## 3.3. Magnetic Properties

Figure4 shows the magnetization (M
-
H) curves obtained for the samples as a function of applied magnetic field. The samples exhibit hysteresis with narrow hysteresis loop and low coercivity, suggesting the soft ferromagnetic nature of the samples. This is due to the formation of the magnetic phase upon heat treatment, as already confirmed by the XRD results.Figure 4
M
-
H curves of the glass ceramic samples with different chemical composition.The different magnetic parameters of the samples are listed in Table5. Sample A1S7 shows higher saturation magnetization M
s (19 emu/g) and remanent magnetization M
r (2.3 emu/g) than the other samples of group A1. This may be due to the enhancement in the magnetic phase in A1S7. However, M
s and M
r values began to decrease when the Fe2O3 content was over 30% (Figure 5), which can be attributed to the higher hematite content and the lower magnetite content. A2P1 has a lower saturation magnetization value but a larger coercive force compared to A1S7. The lower saturation magnetization may be attributed to some possible reactions during the heating process. It is a known fact that P2O5 and SiO2 can easily react with Fe2O3 forming nonmagnetic phases at high temperature [18]. Also, Fe could enter into the crystalline structure forming a solid solution [19]. The coercive field was also influenced in a significant way by the crystal dimensions [20]. The SEM results showed that the average crystallite size of A2P1 was smaller than that of A1S7. The smaller crystallite size of the magnetic phase results in a larger coercive force. These observed phenomena were similar to previous reports [21].Table 5
Magnetic parameters of the samples.
A1S1
A1S3
A1S5
A1S7
A1S9
A2P1
A2P7
H
c (G)
147.76
124.82
206.83
106.24
82.45
113.85
87.87
M
s (emu/g)
1.99
2.06
3.32
19
17.09
10.99
10.65
M
s
∗ (emu/g)
13.27
10.30
13.28
63.33
48.83
36.63
38.04
M
r (emu/g)
0.33
0.41
0.60
2.30
0.78
2.25
3.04
Interpolated hysteresis area
65649
176034
287151
1683193
525486
923229
980057
Note:M
s values were normalized to the total weight of the sample; M
s
∗ values were normalized to the weight of Fe2O3 component alone.Figure 5
Relationship between magnetic properties and the Fe2O3 content.Figure5 shows the relationship between the different magnetic parameters and Fe2O3 content of the samples. The integrated hysteresis loop area was calculated for a maximum applied field of 10000 G. The relationship between integrated loop area and the Fe2O3 content was similar to that observed in the case of saturation magnetization. It can be seen from Figure 5 that the hysteresis loop area of A1S7 with 30% Fe2O3 content is much larger than that of the other samples in group A1, which may be attributed to the higher remanence of A1S7. Theoretically, the energy generated by the glass ceramic samples under low magnetic field can be estimated from the hysteresis loop area [6]. Thus, the above results indicate that A1S7 should be capable of generating a larger amount of heat than the other samples, under a proper alternating magnetic field.


## 3.4. Induction Heating Ability

To test the heating ability of the samples, the induction heating experiments were performed with the different samples. Hyperthermia heating curves, measured at a fixed current of 2 A for 11 min with 1 g concentrations of the samples, are shown in Figure6. The heating rates of the samples were basically the same, and the temperature increased rapidly until 10 min. The temperature variation amplitudes of the samples were found to increase gradually with the increase of Fe2O3 content of the samples. However, the induction heating ability began to fall when the Fe2O3 content was over 30%, which may be caused by the lower magnetite content. Sample A1S7 showed the largest temperature variation amplitudes of 2.7°C in group A1, which is consistent with the results in previous sections. More interestingly, the temperature variation amplitudes of all the samples in group A1 were about 2°C, while the temperature variation amplitudes of the samples in group A2 with phosphorus were as high as 15°C. The addition of phosphorus not only changed the crystalline phase of the samples but also significantly increased their induction heating ability. These results indicate that P2O5-Fe2O3-CaO-SiO2 glass ceramics are more suitable for hyperthermia treatment than Fe2O3-CaO-SiO2 glass ceramics.Figure 6
Temperature evolution as a function of time in the hyperthermia tests.In ferromagnetic materials, heat generation is mainly due to hysteresis loss. In addition, other physical parameters such as particle size and distribution of the components, as well as magnetic field intensity, also considerably influence the heating properties under AC magnetic field. The effect of these factors may be the reason for the ability of group A2 samples to generate more heat than group A1 samples. Further work is in progress in our laboratory to understand the heating properties of this class of glass ceramics and to optimize the composition for therapeutic application.


## 4. Conclusions

Fe2O3-CaO-SiO2 glass ceramics of different compositions were prepared by the sol-gel method and tested for their induction heating ability. Magnetic properties of the glass ceramic samples were found to correlate with the Fe2O3 content. The saturation magnetization and the integrated loop area increased with the magnetite content in A1 group. Thus, the induction heating ability of A1S7 sample was the strongest among all the prepared Fe2O3-CaO-SiO2 glass ceramics. Moreover, the induction heating ability was significantly improved when a small amount of phosphorus was introduced into the Fe2O3-CaO-SiO2 glass ceramics. This reveals a promising methodology to control the magnetic properties of Fe2O3-CaO-SiO2 glass ceramics through the chemical composition and its potential applications in hyperthermia treatment of cancer.



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*Source: 2539468-2016-04-03.xml*