# Preparation of Spherical Zn-Substituted Tricalcium Phosphate Powder by Ultrasonic Spray-Pyrolysis Technique and Its Characterization

Authors: Hiroki Nishikawa; Michiyo Honda; Tomohiro Yokota; Yusuke Shimizu; Mamoru Aizawa
Journal: Journal of Nanomaterials
 (2016)

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## Abstract

Zinc, an essential trace element, has a stimulatory effect on bone formation. To enhance the osteoconduction of implant materials such as hydroxyapatite and tricalcium phosphate (TCP), zinc was incorporated into them. In this study, we have synthesized spherical zinc-substituted TCP (Zn-TCP) powders using ultrasonic spray-pyrolysis technique, fabricated Zn-TCP ceramics, and characterized their powder properties. Four kinds of Zn-TCPs with various amounts of zinc content were prepared, to examine the influence of zinc addition to the crystal structure of TCP and to compare the different Zn-TCPs with each other. Zn-TCP ceramics were fabricated from the resulting powders under different sintering temperatures. Zn-TCP samples were analyzed and led to the following results: the resulting powders were composed ofα- and β-TCP phases, whereas the fabricated ceramics mainly consisted of β-TCP phase. The determination of zinc content in the resulting powders and fabricated ceramics showed a maximum content of ~12 mol%. The resulting powders consisted of spherical particles with diameters <2 μm. The lattice constants of ceramics did not show a significant change of the a-axis, b-axis, and c-axis. The bulk density of Zn-TCPs showed their maximum at 1100°C, while the bulk density of Zn-TCP(0) was greatest at 1000°C.


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## Body

## 1. Introduction

Both hydroxyapatite (HAp; Ca10(PO4)6(OH)2) and tricalcium phosphate (TCP; Ca3(PO4)2) are known for their properties regarding the biocompatibility and osteoconductivity. Moreover, because of their composition, which is close to human hard tissues such as living bones and teeth, they can be used as bone graft substitute materials in medical treatment approaches [1].The HAp is thermodynamically the stable phase at physiological pH and forms a direct chemical bond with hard tissues [2]. On the other hand, the TCP is typically more soluble and less crystalline than HAp, and its cell-mediated bioresorption is faster. Therefore, TCP permits a gradual replacement of the implant by the newly formed bone [3].For the synthesis of such a HAp or TCP powder, one can basically distinguish between two types of preparation methods [4]: the first method is a dry process or a solid-state reaction between calcium and phosphate salts under steam atmosphere. The second one is a wet process or a liquid-phase reaction between calcium and phosphate ions under alkaline conditions. Both of the preparation methods have their advantages and disadvantages. For the preparation of stoichiometric apatite powders, the dry process seems to be an effective method. However, due to the presence of hard agglomerates with undetermined shapes, the resulting powder shows poor sinterability. On the other hand, the HAp powder obtained by a wet process tends to form a nonstoichiometric apatite powder or a calcium-deficient HAp powder, when the conditions for HAp preparations are not strictly controlled, regardless of the excellent sinterability of the resulting powders.In this study, the ultrasonic spray-pyrolysis (USSP) technique was used for the synthesis of TCP powders. The USSP technique is one of the powder preparation methods via the liquid phases [5, 6]. The advantage of this method is that one can prepare stoichiometric and homogeneous compounds instantaneously by spraying the solutions with the desired amounts of cations into the hot zone of an electric furnace. Especially for the preparation of HAp-like materials containing the hydroxyl group in the crystalline structure, this method is effective and the powders can be prepared directly in a steam atmosphere during spray-pyrolysis [7–9].In previous works, the preparation of various calcium phosphates, for example, HAp [7, 9, 10], TCP [11, 12], calcium diphosphate [12], calcium metaphosphate [13], trace elements substituted calcium phosphates such as strontium-substituted HAp [14], silicon-substituted HAp [15], and silver-containing HAp [16] by the USSP technique was reported. The effects of the kinds of the starting materials on properties of HAp powders prepared by the USSP technique were also examined [10].These HAp and TCP possess osteoconductive properties but have no osteoinductive capacity. One solution to develop bone substitutes with osteogenic properties would be to adjust the chemical composition to more closely approximate that of bone mineral [17].Zinc, an essential trace element, is important for growth and stimulation of bone formation. Additionally, zinc could inhibit the effect on osteoclastic bone resorption [18]. Therefore, the release of zinc incorporated into an implant material could enhance the bone formation around the implant site. However, zinc must be released slowly from the implant because zinc at an elevated level induces adverse reactions [19]. For the slow release of zinc, we have chosen β-TCP, which could be the adequate zinc carriers.In the present study, we prepared an essential trace element containing calcium phosphate using the USSP technique, namely, zinc-substituted TCP. The aim of this study was to investigate the effect of zinc incorporation into the TCP structure. Therefore, zinc-containing TCP powders (hereafter, Zn-TCP) and the respective ceramics with various zinc content of 0, 5, 10, or 15 mol% were prepared and subsequently characterized using different analysis methods. Future studies on Zn-TCP will involvein vitro studies to evaluate its biocompatibility and its ability to induce bone formation and inhibit osteoclast bone resorption.


## 2. Materials and Methods

### 2.1. Preparation of Zn-TCP Powders Using USSP Technique and Ceramics Fabrication

As previously reported [14–16], the USSP apparatus was composed of an atomizer, a heating zone (Mullite tube: ID of 2.5 cm and a height of 1 m; electric furnace: ID of 3 cm and a height of 60 cm), a powder collecting zone (test-tube filter), and a controller. The heating section was divided into two electric furnaces: a lower furnace for the evaporation of the solvent from the droplets (temperature: 300°C) and an upper furnace for the pyrolysis (temperature: 1000°C). The aspirator was used to let the droplets be gathered together (suction rate: 2 dm3·min−1).As listed in Table1, four kinds of starting solutions with a ratio of calcium and phosphorus (Ca/P) = 1.5 were prepared by mixing the following compounds: Ca(NO3)2, (NH4)2HPO4, HNO3, and Zn(NO3)2·6H2O.Table 1
Nominal composition of the Zn-TCP starting solutions.
Sample
C
a
(
N
O
3
)
2/mol·dm−3
(
N
H
4
)
2
H
P
O
4/mol·dm−3
H
N
O
3/mol·dm−3
Z
n
(
N
O
3
)
2
·6
H
2
O/mol·dm−3
Z
n
/
m
o
l
%
C
a
/
P
Zn-TCP(0)
0.60
0.40
0.40
—
—
1.50
Zn-TCP(5)
0.60
0.40
0.40
0.01
5
Zn-TCP(10)
0.60
0.40
0.40
0.02
10
Zn-TCP(15)
0.60
0.40
0.40
0.03
15The resulting powders (~5 g) were compressed at 100 MPa to prepare disc shaped green compacts (diameter: ~15 mm; thickness: ~1.5 mm). Those green compacts were sintered at 1000°C, 1100°C, 1200°C, and 1300°C for 5 h (heating rate: 10°C·min−1) to fabricate the respective ceramics.


### 2.2. Characterization of the Resulting Powders and Fabricated Ceramics

Both the crystalline phases of the powders (Miniflex, Rigaku, Japan) and the ceramics (Ultima IV, Rigaku, Japan) were identified by X-ray diffraction (XRD) using CuKα radiation at a range of 2θ = 10–50°, generated at 30 kV and 15 mA with a step size of 2°/min. The crystalline phases were identified on the basis of the JCPDS reference data. The lattice constants in the ceramic structures were calculated by refinement of the collected XRD data. Therefore, the refinement software PDXL was used according to the manufacturer’s instructions (Rigaku).The morphology of the powder particles and ceramics was observed by scanning electron microscope (SEM; JSM-6390LA, JEOL, Japan) at a magnification range of ×5,000 and ×10,000 with an accelerating voltage of 15 kV.The amount of zinc concentration in each powder and ceramic sample was measured by inductive coupled plasma atomic emission spectroscopy (ICP-AES; SPS7800, SII Nanotechnology, Japan).Furthermore, Fourier transform infrared (FT-IR; IR Prestige-21, Shimadzu, Japan) spectra of the powders were recorded in a range of 400–4000 cm−1 by potassium bromide (KBr) pellet method.The median particle size of the powder samples was determined by particle size distribution analysis (PSD; LA-300, Horiba, Japan). Diluting ~0.3 g of each powder in distilled water was measured under an ultrasonic working condition.The bulk density of the fabricated disc shaped ceramics was calculated using the following formula considering diameter, height, and weight of ceramic:(1)
Bulk  density
=
weight  of  ceramic  specimens
g
volume  of  ceramic  specimens
c
m
3
.


## 2.1. Preparation of Zn-TCP Powders Using USSP Technique and Ceramics Fabrication

As previously reported [14–16], the USSP apparatus was composed of an atomizer, a heating zone (Mullite tube: ID of 2.5 cm and a height of 1 m; electric furnace: ID of 3 cm and a height of 60 cm), a powder collecting zone (test-tube filter), and a controller. The heating section was divided into two electric furnaces: a lower furnace for the evaporation of the solvent from the droplets (temperature: 300°C) and an upper furnace for the pyrolysis (temperature: 1000°C). The aspirator was used to let the droplets be gathered together (suction rate: 2 dm3·min−1).As listed in Table1, four kinds of starting solutions with a ratio of calcium and phosphorus (Ca/P) = 1.5 were prepared by mixing the following compounds: Ca(NO3)2, (NH4)2HPO4, HNO3, and Zn(NO3)2·6H2O.Table 1
Nominal composition of the Zn-TCP starting solutions.
Sample
C
a
(
N
O
3
)
2/mol·dm−3
(
N
H
4
)
2
H
P
O
4/mol·dm−3
H
N
O
3/mol·dm−3
Z
n
(
N
O
3
)
2
·6
H
2
O/mol·dm−3
Z
n
/
m
o
l
%
C
a
/
P
Zn-TCP(0)
0.60
0.40
0.40
—
—
1.50
Zn-TCP(5)
0.60
0.40
0.40
0.01
5
Zn-TCP(10)
0.60
0.40
0.40
0.02
10
Zn-TCP(15)
0.60
0.40
0.40
0.03
15The resulting powders (~5 g) were compressed at 100 MPa to prepare disc shaped green compacts (diameter: ~15 mm; thickness: ~1.5 mm). Those green compacts were sintered at 1000°C, 1100°C, 1200°C, and 1300°C for 5 h (heating rate: 10°C·min−1) to fabricate the respective ceramics.


## 2.2. Characterization of the Resulting Powders and Fabricated Ceramics

Both the crystalline phases of the powders (Miniflex, Rigaku, Japan) and the ceramics (Ultima IV, Rigaku, Japan) were identified by X-ray diffraction (XRD) using CuKα radiation at a range of 2θ = 10–50°, generated at 30 kV and 15 mA with a step size of 2°/min. The crystalline phases were identified on the basis of the JCPDS reference data. The lattice constants in the ceramic structures were calculated by refinement of the collected XRD data. Therefore, the refinement software PDXL was used according to the manufacturer’s instructions (Rigaku).The morphology of the powder particles and ceramics was observed by scanning electron microscope (SEM; JSM-6390LA, JEOL, Japan) at a magnification range of ×5,000 and ×10,000 with an accelerating voltage of 15 kV.The amount of zinc concentration in each powder and ceramic sample was measured by inductive coupled plasma atomic emission spectroscopy (ICP-AES; SPS7800, SII Nanotechnology, Japan).Furthermore, Fourier transform infrared (FT-IR; IR Prestige-21, Shimadzu, Japan) spectra of the powders were recorded in a range of 400–4000 cm−1 by potassium bromide (KBr) pellet method.The median particle size of the powder samples was determined by particle size distribution analysis (PSD; LA-300, Horiba, Japan). Diluting ~0.3 g of each powder in distilled water was measured under an ultrasonic working condition.The bulk density of the fabricated disc shaped ceramics was calculated using the following formula considering diameter, height, and weight of ceramic:(1)
Bulk  density
=
weight  of  ceramic  specimens
g
volume  of  ceramic  specimens
c
m
3
.


## 3. Results and Discussion

### 3.1. Characterization of Zn-TCP Powders

The XRD patterns of the resulting Zn-TCP powders are shown in Figure1. As one can see, the crystalline phases were mainly composed of α- and β-TCP phases. However, a little HAp phase was detected in Zn-TCP(5, 10, 15) powders. It is apparent that the peak intensity of β-TCP phase became stronger with increasing zinc concentration at a range of 2θ = 31–32°. Indeed, the ratio of β-TCP phase increased with the increment of Zn concentration. Another aspect was the shifting of the peaks towards higher angles in this range, which is related to the zinc content in the resulting powders. Apparently, the shifting would be related to the change in the size of the unit cell and thus the decrease of the lattice constants with increasing zinc concentration and was also confirmed in other published works [20].Figure 1
The XRD patterns of the resulting Zn-TCP powders derived from various starting solutions: (A) Zn-TCP(0), (B) Zn-TCP(5), (C) Zn-TCP(10), and (D) Zn-TCP(15).FT-IR spectra of the Zn-TCP powders were recorded in a range of 400–4000 cm−1 (Figure 2). The results show the characteristic absorption bands of TCP. The absorptions assigned to the P
O
4
3
- group [21] were detected at 1120–1020 and 600–560 cm−1. The OH− group was detected at ~3420 cm−1 [21]. Either any absorptions assigned to N
O
3
- group or absorptions assigned to the carbonate ion were detected as reported by Monma and Takahashi. Thus, these FT-IR spectra imply an easy preparation of carbonate-free TCP powder by the USSP technique.Figure 2
The FT-IR spectra of the Zn-TCP powders in a range of 400–4000 cm−1: (A) Zn-TCP(0), (B) Zn-TCP(5), (C) Zn-TCP(10), and (D) Zn-TCP(15).The concentrations of Ca, P, and Zn in the Zn-TCP powder samples including the Ca/P and (Ca + Zn)/P ratio were measured by ICP-AES (Table2). The Zn fraction for each composition was represented as ([Zn]/[Ca + Zn]) × 100 (mol%). The comparison between the achieved and expected zinc concentration shows a good approximation under 10 mol% of zinc. It may be connected with the fact that the maximum zinc concentration in Zn-TCP is ~12 mol% [19]. This result could be interpreted as a limitation of zinc incorporation capacity in Zn-TCP.Table 2
Contents of Ca, P, and Zn in the resulting Zn-TCP powders including the Ca/P and (Ca + Zn)/P ratios.
Sample
C
a
/
m
o
l
%
P
/
m
o
l
%
Z
n
/
m
o
l
% (expected)
Z
n
/
m
o
l
% (achieved)
C
a
/
P
(
C
a
+
Z
n
)
/
P
Zn-TCP(0)
59.89 ± 0.18
40.11 ± 0.18
—
—
1.49 ± 0.01
—
Zn-TCP(5)
60.07 ± 0.33
39.84 ± 0.33
5
4.18 ± 0.08
1.51 ± 0.02
1.53 ± 0.02
Zn-TCP(10)
59.69 ± 0.34
40.13 ± 0.36
10
9.21 ± 1.25
1.49 ± 0.02
1.53 ± 0.02
Zn-TCP(15)
59.58 ± 0.69
40.16 ± 0.08
15
12.75 ± 0.41
1.48 ± 0.01
1.55 ± 0.00The morphology of the Zn-TCP powder particles was observed by SEM (Figure3). The SEM micrographs show that all samples consisted of spherical shaped particles with a diameter smaller than 5 μm. The spherical shape of the powder particles could be explained via the following process [22, 23]: (i) removal of the solvent from the droplet surface, (ii) formation of microcrystalline calcium phosphate, and (iii) crystal growth of calcium phosphates. The resulting spherical particle diameters depend on the droplet sizes of the starting solutions, carrier gas, rate of gas flow, or temperature of pyrolysis. Although the droplet size might be changeable with zinc concentration of the starting solutions, no apparent changes were seen in the spherical particle diameters. Moreover, the median particle size of the Zn-TCP powder samples was determined (Figure 4). The median size of each powder was 1.65
±
0.12 μm for Zn-TCP(0), 2.07
±
0.05 μm for Zn-TCP(5), 1.92
±
0.02 μm for Zn-TCP(10), and 1.91
±
0.04 μm for Zn-TCP(15), respectively. There were no significant differences among Zn-TCP(5, 10, or 15) powders regardless of Zn concentration in the starting solution.Figure 3
The SEM micrographs of the resulting Zn-TCP powders: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)Figure 4
The particle size distribution of the resulting Zn-TCP powders: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)


### 3.2. Fabrication of Zn-TCP Ceramics and Their Properties

Figures5(a) and 5(b) show the typical XRD patterns of the fabricated Zn-TCP(0) and Zn-TCP(10) ceramics under different sintering temperatures, respectively. Compared to the phase composition of the resulting powders, the crystalline phase of the Zn-TCP ceramics was mainly composed of β-TCP phase at 1000°C for Zn-TCP(0) and 1100°C for Zn-TCP(10). In addition, Zn-TCP(5) and (15) ceramics were also composed of β-TCP phase at 1100°C (data not shown). These results demonstrated that β-TCP phase in Zn-TCP ceramics could be obtained under 1100°C. Previous report showed that the dominating occurrence of β-TCP phase might be related to the fact that the structure of zinc-substituted β-TCP is more stable than α-TCP [24].Figure 5
The typical XRD patterns of the fabricated (a) Zn-TCP(0) and (b) Zn-TCP(10) ceramics sintered at (A) 1000°C, (B) 1100°C, (C) 1200°C, and (D) 1300°C.
(a)
(b)The contents of Ca, P, and Zn in Zn-TCP ceramics including the Ca/P and (Ca + Zn)/P ratio were determined by ICP-AES (Table3). Compared to the achieved values of the Zn-TCP powders, the concentration of zinc in each ceramic sample was lower. Moreover, the maximum zinc concentration in Zn-TCP ceramic samples also seemed to be ~12 mol% as in the powder samples. These data were consistent with previous study [19].Table 3
Contents of Ca, P, and Zn in the fabricated Zn-TCP ceramics including the Ca/P and (Ca + Zn)/P ratios.
Sample
C
a
/
m
o
l
%
P
/
m
o
l
%
Z
n
/
m
o
l
% (expected)
Z
n
/
m
o
l
% (achieved)
C
a
/
P
(
C
a
+
Z
n
)
/
P
Zn-TCP(0)
59.98 ± 0.25
40.01 ± 0.25
—
—
1.50 ± 0.02
—
Zn-TCP(5)
60.40 ± 0.30
39.52 ± 0.30
5
4.12 ± 0.08
1.53 ± 0.02
1.55 ± 0.02
Zn-TCP(10)
60.18 ± 0.02
39.65 ± 0.01
10
8.50 ± 0.16
1.52 ± 0.00
1.56 ± 0.00
Zn-TCP(15)
59.86 ± 0.26
39.89 ± 0.25
15
12.30 ± 0.71
1.50 ± 0.02
1.56 ± 0.02The morphology of the polished surface of the ceramics derived from the powder samples was observed by SEM (Figure6). Those sintered compacts seemed to be composed of various sized grains. The comparison of Zn-TCP(0) and Zn-TCP(5, 10, 15) clearly showed the difference of the grain size. The grain size of Zn-TCP(5, 10, 15) was smaller than that of Zn-TCP(0). These results indicate that substitution of Zn into β-TCP inhibited the grain growth.Figure 6
The SEM micrographs of the fabricated Zn-TCP ceramics: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)The lattice constants in the crushed ceramic specimens were refined on the basis of the JCPDS reference data by least-squares analysis. The calculated lattice constant ofa, (b)-axis was slightly smaller and that of c-axis was close to the reported ones of the β-TCP structure [25]: a, (b)-axis = 1.04352(2) nm and c-axis = 3.74029(5) nm. It also proves that the fabricated ceramics mainly contained β-TCP phase. An observation of the lattice constants of TCP shows that a, (b) parameters decreased slightly and c parameter did not change significantly (Table 4). Previous investigation demonstrated that decrease of unit cell volume and lattice parameters of β-TCP were attributed by Zn2+ substitution for Ca2+ in the calcium sites of the β-TCP structure [26]. Compared with previous reports, Zn will be solid-soluted into β-TCP structure.Table 4
The value of the lattice constants in the fabricated Zn-TCP ceramic samples.
Sample
a, (b)-axis/nm
c
-
a
x
i
s
/
n
m
Zn-TCP(0)
1.0429 ± 0.0051
3.7340 ± 0.0184
Zn-TCP(5)
1.0416 ± 0.0016
3.7380 ± 0.0161
Zn-TCP(10)
1.0426 ± 0.0015
3.7387 ± 0.0250
Zn-TCP(15)
1.0421 ± 0.0036
3.7371 ± 0.0136The relationship between the sintering temperature and the bulk density of the fabricated Zn-TCP ceramics was shown in Figure7. The bulk density of Zn-TCP(0) was the greatest at 1000°C and then decreased slightly. Over 1100°C, the proportion of α-TCP in Zn-TCP(0) increased (Figure 5(a)). Transformation of β-TCP to α-TCP phase might affect the decrease of bulk density. On the other hand, the bulk density of Zn-TCP(5, 10, 15) ceramics at 1100°C increased compared with that at 1000°C. These results implied that Zn-TCP(5, 10, 15) ceramics were not sintered completely at 1000°C (Figure 5(b)). However, at the temperatures 1100–1300°C, no apparent changes of bulk density among Zn-TCP(5, 10, 15) ceramics were seen. In addition, from SEM images, it can be seen that a small amount of micropores exists on the surface of ceramics. These data revealed that the structure of microspheres makes it difficult to obtain high bulk density of ceramics.Figure 7
The relationship between the sintering temperature and the bulk density of the fabricated Zn-TCP ceramics.


## 3.1. Characterization of Zn-TCP Powders

The XRD patterns of the resulting Zn-TCP powders are shown in Figure1. As one can see, the crystalline phases were mainly composed of α- and β-TCP phases. However, a little HAp phase was detected in Zn-TCP(5, 10, 15) powders. It is apparent that the peak intensity of β-TCP phase became stronger with increasing zinc concentration at a range of 2θ = 31–32°. Indeed, the ratio of β-TCP phase increased with the increment of Zn concentration. Another aspect was the shifting of the peaks towards higher angles in this range, which is related to the zinc content in the resulting powders. Apparently, the shifting would be related to the change in the size of the unit cell and thus the decrease of the lattice constants with increasing zinc concentration and was also confirmed in other published works [20].Figure 1
The XRD patterns of the resulting Zn-TCP powders derived from various starting solutions: (A) Zn-TCP(0), (B) Zn-TCP(5), (C) Zn-TCP(10), and (D) Zn-TCP(15).FT-IR spectra of the Zn-TCP powders were recorded in a range of 400–4000 cm−1 (Figure 2). The results show the characteristic absorption bands of TCP. The absorptions assigned to the P
O
4
3
- group [21] were detected at 1120–1020 and 600–560 cm−1. The OH− group was detected at ~3420 cm−1 [21]. Either any absorptions assigned to N
O
3
- group or absorptions assigned to the carbonate ion were detected as reported by Monma and Takahashi. Thus, these FT-IR spectra imply an easy preparation of carbonate-free TCP powder by the USSP technique.Figure 2
The FT-IR spectra of the Zn-TCP powders in a range of 400–4000 cm−1: (A) Zn-TCP(0), (B) Zn-TCP(5), (C) Zn-TCP(10), and (D) Zn-TCP(15).The concentrations of Ca, P, and Zn in the Zn-TCP powder samples including the Ca/P and (Ca + Zn)/P ratio were measured by ICP-AES (Table2). The Zn fraction for each composition was represented as ([Zn]/[Ca + Zn]) × 100 (mol%). The comparison between the achieved and expected zinc concentration shows a good approximation under 10 mol% of zinc. It may be connected with the fact that the maximum zinc concentration in Zn-TCP is ~12 mol% [19]. This result could be interpreted as a limitation of zinc incorporation capacity in Zn-TCP.Table 2
Contents of Ca, P, and Zn in the resulting Zn-TCP powders including the Ca/P and (Ca + Zn)/P ratios.
Sample
C
a
/
m
o
l
%
P
/
m
o
l
%
Z
n
/
m
o
l
% (expected)
Z
n
/
m
o
l
% (achieved)
C
a
/
P
(
C
a
+
Z
n
)
/
P
Zn-TCP(0)
59.89 ± 0.18
40.11 ± 0.18
—
—
1.49 ± 0.01
—
Zn-TCP(5)
60.07 ± 0.33
39.84 ± 0.33
5
4.18 ± 0.08
1.51 ± 0.02
1.53 ± 0.02
Zn-TCP(10)
59.69 ± 0.34
40.13 ± 0.36
10
9.21 ± 1.25
1.49 ± 0.02
1.53 ± 0.02
Zn-TCP(15)
59.58 ± 0.69
40.16 ± 0.08
15
12.75 ± 0.41
1.48 ± 0.01
1.55 ± 0.00The morphology of the Zn-TCP powder particles was observed by SEM (Figure3). The SEM micrographs show that all samples consisted of spherical shaped particles with a diameter smaller than 5 μm. The spherical shape of the powder particles could be explained via the following process [22, 23]: (i) removal of the solvent from the droplet surface, (ii) formation of microcrystalline calcium phosphate, and (iii) crystal growth of calcium phosphates. The resulting spherical particle diameters depend on the droplet sizes of the starting solutions, carrier gas, rate of gas flow, or temperature of pyrolysis. Although the droplet size might be changeable with zinc concentration of the starting solutions, no apparent changes were seen in the spherical particle diameters. Moreover, the median particle size of the Zn-TCP powder samples was determined (Figure 4). The median size of each powder was 1.65
±
0.12 μm for Zn-TCP(0), 2.07
±
0.05 μm for Zn-TCP(5), 1.92
±
0.02 μm for Zn-TCP(10), and 1.91
±
0.04 μm for Zn-TCP(15), respectively. There were no significant differences among Zn-TCP(5, 10, or 15) powders regardless of Zn concentration in the starting solution.Figure 3
The SEM micrographs of the resulting Zn-TCP powders: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)Figure 4
The particle size distribution of the resulting Zn-TCP powders: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)


## 3.2. Fabrication of Zn-TCP Ceramics and Their Properties

Figures5(a) and 5(b) show the typical XRD patterns of the fabricated Zn-TCP(0) and Zn-TCP(10) ceramics under different sintering temperatures, respectively. Compared to the phase composition of the resulting powders, the crystalline phase of the Zn-TCP ceramics was mainly composed of β-TCP phase at 1000°C for Zn-TCP(0) and 1100°C for Zn-TCP(10). In addition, Zn-TCP(5) and (15) ceramics were also composed of β-TCP phase at 1100°C (data not shown). These results demonstrated that β-TCP phase in Zn-TCP ceramics could be obtained under 1100°C. Previous report showed that the dominating occurrence of β-TCP phase might be related to the fact that the structure of zinc-substituted β-TCP is more stable than α-TCP [24].Figure 5
The typical XRD patterns of the fabricated (a) Zn-TCP(0) and (b) Zn-TCP(10) ceramics sintered at (A) 1000°C, (B) 1100°C, (C) 1200°C, and (D) 1300°C.
(a)
(b)The contents of Ca, P, and Zn in Zn-TCP ceramics including the Ca/P and (Ca + Zn)/P ratio were determined by ICP-AES (Table3). Compared to the achieved values of the Zn-TCP powders, the concentration of zinc in each ceramic sample was lower. Moreover, the maximum zinc concentration in Zn-TCP ceramic samples also seemed to be ~12 mol% as in the powder samples. These data were consistent with previous study [19].Table 3
Contents of Ca, P, and Zn in the fabricated Zn-TCP ceramics including the Ca/P and (Ca + Zn)/P ratios.
Sample
C
a
/
m
o
l
%
P
/
m
o
l
%
Z
n
/
m
o
l
% (expected)
Z
n
/
m
o
l
% (achieved)
C
a
/
P
(
C
a
+
Z
n
)
/
P
Zn-TCP(0)
59.98 ± 0.25
40.01 ± 0.25
—
—
1.50 ± 0.02
—
Zn-TCP(5)
60.40 ± 0.30
39.52 ± 0.30
5
4.12 ± 0.08
1.53 ± 0.02
1.55 ± 0.02
Zn-TCP(10)
60.18 ± 0.02
39.65 ± 0.01
10
8.50 ± 0.16
1.52 ± 0.00
1.56 ± 0.00
Zn-TCP(15)
59.86 ± 0.26
39.89 ± 0.25
15
12.30 ± 0.71
1.50 ± 0.02
1.56 ± 0.02The morphology of the polished surface of the ceramics derived from the powder samples was observed by SEM (Figure6). Those sintered compacts seemed to be composed of various sized grains. The comparison of Zn-TCP(0) and Zn-TCP(5, 10, 15) clearly showed the difference of the grain size. The grain size of Zn-TCP(5, 10, 15) was smaller than that of Zn-TCP(0). These results indicate that substitution of Zn into β-TCP inhibited the grain growth.Figure 6
The SEM micrographs of the fabricated Zn-TCP ceramics: (a) Zn-TCP(0), (b) Zn-TCP(5), (c) Zn-TCP(10), and (d) Zn-TCP(15).
(a)
(b)
(c)
(d)The lattice constants in the crushed ceramic specimens were refined on the basis of the JCPDS reference data by least-squares analysis. The calculated lattice constant ofa, (b)-axis was slightly smaller and that of c-axis was close to the reported ones of the β-TCP structure [25]: a, (b)-axis = 1.04352(2) nm and c-axis = 3.74029(5) nm. It also proves that the fabricated ceramics mainly contained β-TCP phase. An observation of the lattice constants of TCP shows that a, (b) parameters decreased slightly and c parameter did not change significantly (Table 4). Previous investigation demonstrated that decrease of unit cell volume and lattice parameters of β-TCP were attributed by Zn2+ substitution for Ca2+ in the calcium sites of the β-TCP structure [26]. Compared with previous reports, Zn will be solid-soluted into β-TCP structure.Table 4
The value of the lattice constants in the fabricated Zn-TCP ceramic samples.
Sample
a, (b)-axis/nm
c
-
a
x
i
s
/
n
m
Zn-TCP(0)
1.0429 ± 0.0051
3.7340 ± 0.0184
Zn-TCP(5)
1.0416 ± 0.0016
3.7380 ± 0.0161
Zn-TCP(10)
1.0426 ± 0.0015
3.7387 ± 0.0250
Zn-TCP(15)
1.0421 ± 0.0036
3.7371 ± 0.0136The relationship between the sintering temperature and the bulk density of the fabricated Zn-TCP ceramics was shown in Figure7. The bulk density of Zn-TCP(0) was the greatest at 1000°C and then decreased slightly. Over 1100°C, the proportion of α-TCP in Zn-TCP(0) increased (Figure 5(a)). Transformation of β-TCP to α-TCP phase might affect the decrease of bulk density. On the other hand, the bulk density of Zn-TCP(5, 10, 15) ceramics at 1100°C increased compared with that at 1000°C. These results implied that Zn-TCP(5, 10, 15) ceramics were not sintered completely at 1000°C (Figure 5(b)). However, at the temperatures 1100–1300°C, no apparent changes of bulk density among Zn-TCP(5, 10, 15) ceramics were seen. In addition, from SEM images, it can be seen that a small amount of micropores exists on the surface of ceramics. These data revealed that the structure of microspheres makes it difficult to obtain high bulk density of ceramics.Figure 7
The relationship between the sintering temperature and the bulk density of the fabricated Zn-TCP ceramics.


## 4. Conclusions

On the basis of the characterization of the synthesized Zn-TCP powders and respective ceramics, it was possible to determine to what extent the incorporation of zinc ions in TCP structure influences the chemical properties of TCP. The results can be summarized as follows:(i)
The crystalline phases of the Zn-TCP powders consisted ofα-, β-TCP, and HAp phases. On the other hand, the Zn-TCP ceramics were almost composed of β-TCP phase.
(ii)
The FT-IR spectra of the resulting Zn-TCP powders showed the characteristic absorption bands of TCP.
(iii)
Contents of Ca, P, and Zn in Zn-TCP powders and ceramics via ICP-AES showed the effectivity of the USSP technique for the synthesis of calcium phosphates with the desired stoichiometric composition.
(iv)
The resulting Zn-TCP powders were composed of spherical shaped particles with a diameter smaller than 2μm, whereas the median size grew with increasing zinc concentration. On the other hand, the microstructure of the Zn-TCP ceramics consisted of various sized grains. The grain size was affected by the incorporation of zinc ions into the TCP crystal structure. As a result, the grain size of Zn-TCP(5, 10, 15) was smaller than that of Zn-TCP(0).
(v)
The calculated lattice constants in the Zn-TCP ceramic samples indicated that the sintered compacts mainly containedβ-TCP phase. However, the increasing zinc content only slightly affected the values of the a-axis, b-axis.
(vi)
The relationship between the sintering temperatures and the bulk density showed that the bulk density of Zn-TCP(5), (10), and (15) was the highest at 1100°C and then reached plateau. However, the bulk density of Zn-TCP(0) was the highest at 1000°C and then decreased slightly.



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*Source: 6753203-2016-03-10.xml*