Advances in Materials Science and Engineering
Volume 2017 (2017), Article ID 9523174, 7 pages
https://doi.org/10.1155/2017/9523174

Research Article

Study on the Effect of Different Fe₂O₃/ZrO₂ Ratio on the Properties of Silicate Glass Fibers

Jianxun Liu,1,2 Jianping Yang,² Haibin Huo,¹ Liang Lei,² Ying Cui,² and Zhishen Wu1,2

¹International Institute for Urban Systems Engineering, Southeast University, Nanjing 210096, China
²National & Local Joint Engineering Research Center of “Basalt Fiber Production and Application”, Southeast University, Nanjing 210096, China

Correspondence should be addressed to Zhishen Wu; zswu@seu.edu.cn

Received 14 April 2017; Accepted 21 August 2017; Published 28 September 2017

Academic Editor: Belal F. Yousif

Copyright © 2017 Jianxun Liu et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

A series of silicate glass fibers with different ratios of Fe₂O₃/ZrO₂ were prepared, and their corrosion resistance, mass loss, and strength loss were characterized. The crystallization and melting properties of the fibers were analyzed by differential scanning calorimetry (DSC), high temperature viscometer, and high temperature microscope. The results show that the deformation temperature, sphere temperature, hemisphere temperature, and crystallization temperature of the fiber initially decrease and then increase with the increase of Fe₂O₃/ZrO₂ ratio, while the molding temperature decreases with the increase of the ratio of Fe₂O₃/ZrO₂. When the ratio is close to 1 : 1, its alkali resistance is almost same as that of AR-glass fiber, and the drawing process performance is better. However, with the increase of the ratio, its alkali resistance continues to decline and the poor wire drawing performance is not conducive to the drawing operation.

1. Introduction

Basalt fiber is a new kind of inorganic nonmetallic silicate fiber prepared by melt drawing process with natural basalt ores as raw materials [1, 2]. Compared with ordinary glass fiber, basalt fiber has excellent high tensile strength, elastic modulus, creep resistance, fatigue resistance, high temperature resistance, and other properties [3, 4] and is generally considered as a material with excellent alkali resistance [5–8], which could be widely used in many fields such as civil engineering, transportation, and marine engineering [9, 10].

Most silicate glass fiber is easily eroded by alkali in alkaline environment, such as ordinary alkali-free glass fiber and high strength glass fiber. In the 1970s the British Pilkington company invented alkali resistant glass fiber and improved the alkali resistance of fiber [11], which solved the problems of strength reduction, cracking, and leakage of the ordinary glass fiber due to the alkaline reaction with cement. However, the raw materials for alkali resistant glass fiber are very expensive, which limits its wide application.

By comparison of the components of basalt fiber and alkali resistant glass fiber, it can be concluded that the characteristic component of basalt fiber is Fe₂O₃ and the characteristic component of alkali resistant glass fiber is ZrO₂. Referring to the solubility product constant table, the solubility product constants of Fe(OH)₃ and ZrO(OH)₂ are and , respectively, which are both very small. Therefore, it can be also understood for the mechanism of alkali erosion that Fe₂O₃ on the fiber surface will be converted to Fe(OH)₃ jelly under the action of alkali solution and form a dense film on glass surface through dehydration polymerization, which can prevent the erosion to fiber from the alkali solution and hydrate. Similarly, when the alkali resistant glass fiber is in alkaline solution, ZrO₂ on the fiber surface will be converted to ZrO(OH)₂ jelly and form a dense film on glass surface to prevent the erosion [12].

The alkali resistant glass fiber contains ZrO₂ with absence of Fe₂O₃, while basalt fiber contains Fe₂O₃ without ZrO₂. In recent years, Lipatov et al. studied the influence of ZrO₂ on the alkali resistance, mechanical properties, and crystallization properties of basalt fiber [13, 14].

In this paper, based on the small solubility product constant of Fe(OH)₃ and ZrO(OH)₂ and the formation of a protective film on the glass fiber surface, silicate glass fibers with different ratios of Fe₂O₃/ZrO₂ were prepared, and the effect of different Fe₂O₃/ZrO₂ ratio on alkali resistance fiber and its drawing process performance was investigated.

2. Experimental

2.1. Ingredient Formulae

As showed in Table 1, a composition scheme with various proportions of Fe₂O₃/ZrO₂ was designed in which the contents of SiO₂, Al₂O₃, CaO, MgO, K₂O, Na₂O, and TiO₂ kept unchanged. Basalt ore was used as main raw material, and quartz sand, zircon, industrial grade iron oxide, alumina, magnesium oxide, calcium oxide, sodium carbonate, and potassium carbonate were used as auxiliary raw material, among which zircon was used to introduce ZrO₂ while basalt ore and industrial iron were used to introduce Fe₂O₃.

Table 1: Chemical composition of samples (wt%).

Component
1#
2#
3#
4#
E-glass  
AR-glass  

SiO₂
61.00
61.00
61.00
61.00
54.35
62

Al₂O₃
0.50
0.50
0.50
0.50
14.90
1.0

CaO
5.80
5.80
5.80
5.80
16.60
4

MgO
0.80
0.80
0.80
0.80
4.6
/

K₂O
2.50
2.50
2.50
2.50
0.15
3.0

Na₂O
13.00
13.00
13.00
13.00
0.15
11

TiO₂
1.00
1.00
1.00
1.00
0.49
5

ZrO₂
16.00
12.00
8.00
4.00
/
14

Fe₂O₃
0.20
4.20
8.20
12.20
0.21
/

B₂O₃
/
/
/
/
8.7
/

2.2. Preparation Process

The raw materials were weighed according to Table 1, mixed uniformly, and melted in the home-made platinum crucible. Melting was kept at °C for 24 hours with continuous stirring to obtain a clarified and homogenized glass melt, which was then poured on to a heat resistant steel plate and cooled down to obtain a glass block as the samples. The samples were placed in a self-designed drawing crucible for wire drawing, and the sample fibers with required diameters were obtained by adjusting the temperature of the magma, the height of the liquid surface, and the speed of the wire drawing machine.

2.3. The Testing Process

The alkali resistance of glass samples was evaluated by two methods: mass loss and strength retention. The mass and strength of the samples before and after the alkali etching were measured by the electronic analytical balance (Shanghai JA1003) and the fiber tensile tester (Shanghai Institute of Applied Science and Technology, XQ-1A), respectively. And the mass loss rate was calculated according to (1) (: mass of samples before etching with an alkaline solution; : mass of samples after etching with an alkaline solution). The strength retention rate was calculated according to (2) (: fiber strength before alkali solution erosion; : fiber strength after alkali solution erosion).

The crystallization temperature of the glass samples was measured by a differential scanning calorimetry (DSC, DSC200F3Maia). The high temperature viscosity and melting properties of the glass samples were measured by high temperature rotational viscometer (Rheoteonic II) and high temperature microscope (OCA20LHT), respectively.

3. Results and Discussion

3.1. Effect of Fe₂O₃/ZrO₂ on Crystalline Phase of Samples

Silicate glass fiber is a product of high temperature melting and drawing. In order to investigate whether the process contains undamaged mineral phase or crystalline phase, the fiber was analyzed by X-ray diffraction, as shown in Figure 1. Therefore, the fiber was analyzed by X-ray diffraction and was shown in Figure 1. It can be seen from Figure 1 that the X-ray diffraction pattern of the fiber has only steamed bread peaks similar to glass. This shows that silicate glass fibers do not have any mineral phases and crystalline phases and exist in the form of amorphous.

Figure 1: X-ray diffraction pattern of fiber samples.

3.2. Effect of Fe₂O₃/ZrO₂ on Mass Loss Rate of Samples

The melted glass pieces were crushed and the granules were sieved through a 20–40 mesh sieve to obtain powder samples. Samples with known mass () were placed in a conical flask of 2 mol/L NaOH solution and then placed in a water bath at a constant temperature of °C. The conical flasks were connected to a reflux condenser and sealed with plastic wrap. After 24 h, the powder was weighed again to obtain its mass (), and the mass loss rate was calculated. The measured data were presented in Table 2, and the mass loss rate of each sample was shown in Figure 2.

Table 2: Mass and mass loss rate of samples before and after corrosion in NaOH solution.

Sample
1#
2#
3#
4#
E-glass
AR-glass

/g
10.5452
10.5235
10.5134
10.5012
10.5418
10.5057

/g
10.4693
10.4382
10.4083
10.3752
10.2761
10.4090

Mass loss rate/%
0.72
0.81
1.00
1.20
2.52
0.92

Figure 2: Mass loss rate of samples after corrosion in NaOH solution (unit: %).

The weight loss rate of 1# sample is the smallest, the weight loss rates of 1#~4# samples increase with the increase of Fe₂O₃/ZrO₂ ratio, and the weight loss rate of 3# is close to that of AR-glass indicating that their alkali resistances are almost equal. The weight loss rate of the E-glass without ZrO₂ and Fe₂O₃ is the highest, which indicates that the E-glass is most resistant to alkali attack.

3.3. Effect of Fe₂O₃/ZrO₂ on Strength Retention of Samples

Prepared fibers were immersed in Ca(OH)₂ saturated solution and heated at °C for 4 h. The tensile strength of the fibers before and after etching was measured according to ASTMD3379-75. A single fiber was bonded to the board, as shown in Figure 3. The experiment was carried out by using the 100 cN sensor tensile tester and the testing speed was 2 mm/min. During the test, once the fiber was fixed by the instrument, both sides of the cardboard were cut off with the scissors. For each fiber sample, 25 effective strength values were recorded and then were averaged. The tensile strength retention rates are calculated and presented in Table 3. The trend of strength retention rate is shown in Figure 4.

Table 3: Tensile strength and strength retention rate of samples before and after corrosion in saturated Ca(OH)₂ solution.

Sample
1#
2#
3#
4#
E-glass
AR-glass

/MPa
2936.72
2798.74
2240.21
1804.86
2340.27
2417.90

/MPa
2780.49
2468.69
1889.44
1338.11
1538.56
2032.74

Strength retention rate/%
94.68
88.21
84.34
74.14
65.74
84.07

Figure 3: Tensile test specimen of fibers.

Figure 4: Strength retention rate of samples after corrosion in saturated Ca(OH)₂ solution.

It can be seen that the tensile strength of the 1# sample is the highest before the alkali etching, and the retention rate of the strength after the alkali erosion is the largest. The strength retention rates of 1#~4# samples decrease with the increase of the ratio of Fe₂O₃/ZrO₂, and the strength retention rate of 3# is most close to that of AR-glass fibers, indicating that the alkali resistance of the two samples is the same. E-glass fibers do not contain ZrO₂ and Fe₂O₃, so its strength retention rate is the lowest indicating the worst alkali resistance. Reference [13] mentions that the addition of less than 3.1 wt% ZrO₂ increases the alkali resistance of the basalt fibers by 37%. The addition of more than 3.1 wt% ZrO₂ to the glass batch reduces the alkali resistance and tensile strength of the basalt fibers. Compared with this paper, there are some differences in data. The reason may be that the chemical composition of the sample is different.

In summary, the addition of ZrO₂ in the glass could significantly improve the alkali resistance of the glass system, because the ZrO₂ on the glass surface will be converted into ZrO(OH)₂ jelly and form a layer of dense membrane on the glass surface by dehydration polymerization to make it more resistant to the corrosion of the alkali solution and other hydrides [12–17]. The mass loss rate and strength retention rate of the glass samples decrease with the increase of the ratio of Fe₂O₃/ZrO₂. It is worth noting that when the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1 (3# sample), the mass loss rate and strength retention rate are almost the same as those of AR-glass. The results show that 3# and AR-glass have the similar ability to resist alkali corrosion. In glass system, Fe³⁺ exists in two states: [FeO₄] and [FeO₆] [18, 19]; when a monovalent alkali metal ions or divalent alkali metal ions exist, Fe³⁺ will form [FeO₄] tetrahedron and get into the -Si-O-Si- network as a network connector, so that the structure of the glass becomes tighter. On the contrary when there are no monovalent alkali metal ions and divalent alkali metal ions or the ion concentration is low, Fe³⁺ would be in the glass network gap to form [FeO₆] octahedron. At the same time, Fe³⁺ ions also have a certain accumulation effect on the oxygen ions in the [SiO₄] tetrahedron, which makes the structure denser [20]. Both of them could prevent further corrosion of the alkali solution on the fiber surface and the stability of the vitreous structure will not be broken. The relevant research has been carried out by Hwang and Lim [21], and it is considered that the oxidation state of iron has the following dynamic equilibrium relation.

Because the pure FeO does not exist in nature, when the temperature reaches 1475°C, part of Fe₂O₃ would be broken down and release oxygen to form Fe²⁺, so Fe²⁺ and Fe³⁺ will always coexist in the silicate glass and the ratio varies with the melting conditions.

An important structure of ferrous ferrite (Fe³⁺-O-Fe²⁺) forms, when Fe³⁺ and Fe²⁺ coexist in a silicate glass system. When Fe³⁺ ions in Fe³⁺-O-Fe²⁺ structure are in tetrahedral coordination, they act as the network formers, while when Fe²⁺ ions are in octahedral coordination they are the network modifiers. When there are excess Fe³⁺ ions, the excess Fe³⁺ could only be in octahedral coordination network modifier position, and the formation of Si⁴⁺-O-Fe³⁺ structure could make the fiber has tighter structure, better chemical stability, and better mechanical performance. On the other hand, when there are excess Fe²⁺ ions, the excess Fe²⁺ are also in octahedral coordination network modifier position, and the formation of Si⁴⁺-O-Fe²⁺ structure could also prevent further erosion of the alkali solution on the fiber surface.

3.4. Effect of Fe₂O₃/ZrO₂ on Crystallization Behavior of Samples

The glass transition temperature and the crystallization exothermic peak temperature [22] of the glass samples were measured at the heating rate of 10°C/min in the high purity nitrogen atmosphere, which are shown in Table 4 and in Figure 5.

Table 4: Crystallization properties of samples.

Sample
/°C
/°C
/°C

1#
711.35
1062.15
350.8

2#
637.75
1036.05
398.3

3#
674.45
1044.55
370.1

4#
719.25
1059.35
340.1

E-glass
694.55
966.75
272.2

AR-glass
741.35
1042.95
301.6

Figure 5: DSC curves of fibers.

It could be seen that the glass transition temperature initially decreases from 711.35°C to 637.75°C and then rises to 719.25°C, and the crystallization exothermic peak temperature also decreases from 1062.15°C to 1036.05°C and then rises to 1059.35°C. These results indicate that and have a parabola-like trend with the increase of Fe₂O₃/ZrO₂. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 3, and reach the minimum values of 637.75°C and 1036.05°C respectively, and then and begin to rise again. When the ratio of Fe₂O₃/ZrO₂ is less than 1 : 3, the crystallization temperature of the glass samples is reduced, and the crystallization ability is improved. Furthermore, when the ratio of Fe₂O₃/ZrO₂ is more than 1 : 3, the crystallization temperature of glass samples begins to increase, and the crystallization ability is reduced. This is because Fe³⁺ is mainly present in the form of [FeO₄] when Fe₂O₃ is initially added. Fe³⁺ has an internal polarization effect on the network frame of silicate glass, which makes the network connected tightly, the viscosity of silicate glass increased, and the crystallization ability enhanced. With the increase of the content of Fe³⁺, Fe₂O₃ would be mainly [FeO₆], manifesting as the increase of the external polarization, which results in gradually loosed network structure of silicate glass, the reduced viscosity, and the reduced crystallization ability. At the same time, of 3# and AR-glass are not significantly different, while of 3# is significantly lower than that of the AR-glass. Therefore, liquid phase is easier to form in the 3# sample during the melting process which can reduce energy consumption. Reference [13] mentions that when the content of ZrO₂ increases from 0 to 6.9 wt%, increases from 940°C to 1005°C. The results show that and increase with the increase of ZrO₂ content. The results of this study are consistent with our study.

3.5. Effect of Fe₂O₃/ZrO₂ on High Temperature Viscosity of Samples

The high temperature viscosity of glass samples was tested. The viscosity-temperature curve is shown in Figure 6, and the corresponding temperature for the samples at is shown in Table 5.

Table 5: Molding temperature of the samples (unit: C).

Sample

1#
1379.23

2#
1348.55

3#
1318.9

4#
1260.54

E-glass
1256.67

AR-glass
1356.71

Figure 6: Viscosity-temperature curve of samples.

Considering the inclinations of the curves in Figure 4, the viscosity of 1# has the largest changing trend as the temperature decreases, followed by 2#, 3#, and 4# successively. The viscosity-temperature curve of E-glass is smooth and the viscosity is small. The trends of viscosity curves of AR-glass and 1# samples are basically the same, which might be due to the similar ZrO₂ content of 1# and AR-glass. ZrO₂ is octahedral coordination (), and the radius of Zr⁴⁺ is large. Under the same electric charge condition, with the increase of the coordination number () of the cation in the glass melt, the accumulation of silicon oxygen groups is enhanced and then the viscosity increases. Therefore, the viscosity of 1# and AR-glass is relatively larger. The viscosity of 3# is significantly better than that of AR-glass, which could meet the test results of crystallization properties of glass samples.

As shown in Table 5, with the increase of the ratio of Fe₂O₃/ZrO₂ in the glass samples, the corresponding temperature of log decreases, which is the drawing molding temperature. At this time, the drawing molding temperature of 3# is obviously lower than that of AR-glass, which could be beneficial to energy saving and production cost reduction.

3.6. Effect of Fe₂O₃/ZrO₂ on High Temperature Melting of Samples

The glass samples were placed in a furnace and heated up at a rate of 10°C/min. The deformation temperature (DT), sphere temperature (ST), and hemisphere temperature (HT) of the glass samples are plotted in Figure 7. The melting states of the glass samples at different temperatures are shown in Figure 8.

Figure 7: Melting temperature curve of samples.

Figure 8: Melting state of samples.

From Figure 8, it could be seen that the DT, ST, and HT of the glass samples initially decrease and then increase with the increase of Fe₂O₃/ZrO₂, and the change trend is presented in Figure 5. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1, the DT, ST, and HT decline to the lowest temperature. Therefore, the melting temperature of 3# is the lowest. Compared with AR-glass, 3# has lower melting temperature, which is accordant with the results of high temperature viscosity test.

When the Fe₂O₃ content in the glass samples increases, the ZrO₂ content will decrease, which results in the change trend of the melting temperature of 1#~4# samples. Zr⁴⁺ is present in the form of [ZrO₆] octahedral in the zirconium silicate melts. There are at least two silicon oxygen tetrahedrons between Zr⁴⁺ ions, and the bond strength of Zr-O-Si bond is high and is not readily destroyed at higher temperature. As a result, the melting temperatures of 1# and AR-glass are higher, while the melting temperatures of 2#, 3#, and 4# decrease with the decrease of ZrO₂ content (increasing ratio of Fe₂O₃/ZrO₂). At the same time, with the decrease of ZrO₂ content it is also accompanied by the increase of Fe₂O₃ content. Fe³⁺ is mainly present in the form of [FeO₄] when Fe₂O₃ is added initially. Fe³⁺ has an internal polarization effect on the network frame of silicate glass, which makes the network connected tightly, so that the melting temperatures of 1# and AR-glass are higher. With the increasing content of Fe³⁺, Fe₂O₃ would be mainly in the form of [FeO₆], which manifests as the increase of the external polarization, results in the gradually loosed network structure of silicate glass, and further causes the decrease of the melting temperature.

4. Conclusions

With the increase of Fe₂O₃/ZrO₂ ratio, the alkali resistance of silicate glass fiber decreases. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1, the alkali resistances of 3# and AR-glass are almost same and are much higher than that of E-glass.

With the increase of Fe₂O₃/ZrO₂ ratio, the crystallization temperature of silicate glass shows a trend of decreasing first and then increasing. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1, of 3# and AR-glass are almost same, while is significantly lower than that of AR-glass. Therefore, the 3# has better crystallization properties compared with AR-glass.

With the increase of Fe₂O₃/ZrO₂ ratio, the viscosities of 1# and AR-glass are the highest, and the viscosities of 2#, 3#, 4#, and E-glass decrease in sequence. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1, 3# has lower viscosity and drawing molding temperature compared with AR-glass, and the wire drawing is easier in the process of fiber preparation.

With the increase of Fe₂O₃/ZrO₂ ratio, the DT, ST, and HT of silicate glass initially decrease and then increase. When the ratio of Fe₂O₃/ZrO₂ is close to 1 : 1, the DT, ST, and HT of 3# have the lowest values, and 3# sample has a lower melting temperature compared with AR-glass, which could save energy consumption and reduce the production cost.

If Fe₂O₃ is used to replace a part of ZrO₂, the AR-glass fiber still has good melting characteristics, chemical corrosion resistance, and mechanical properties, which could greatly reduce the production cost of AR-glass fiber.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

The authors gratefully acknowledge the financial support provided by the Nature Science Foundation of Jiangsu Province, China (Grant no. BK20130623), and Production and School Joint Research Innovation Fund in Jiangsu Province, China (Grant no. BY2013079).

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