Active energy and proportional coefficient for crack-healing
The heat-resistant limit of structural ceramics is 1273K ~ 1773K, which is greatly superior to that of metallic material. Structural ceramics are a candidate element for high-temperature apparatuses such as gas-turbines and fusion reactors. However, the fracture toughness of ceramics is fairly low compared with metallic material, and the following problems have occurred.
Cracks occur by the usual machining process (grinding, polish, etc.), lowering the reliability. In order to prevent this, precise polishing is required in the final stage, which is time-consuming, and there are also problems with fabrication efficiency and fabrication cost
Crack sizes of about 10 ~ 30 μm in depth affect the reliability. The nondestructive-inspection technology for detecting cracks of 10 ~ 30 μm is underdeveloped. Therefore, the reliability of major parts is low.
There is a possibility that a crack will occur in the components while they are being used at higher temperatures, by whatever cause. When a crack occurs, the reliability is greatly lowered.
The options for resolving these problems are as follows.
Improve the fracture toughness of the material by such means as microstructure control and fiber reinforcement.
Conduct a nondestructive inspection before use, and detect and repair any dangerous cracks found.
Conduct a proof test to prevent use of a low reliability member.
Induce a self-crack-healing ability, so that all dangers cracks can be healed.
There are world-wide active investigations of options (a) to (c). In this chapter, special attention is paid to method (d), the self–crack-healing ability of structural ceramics.
There are three advantages to using a material that can heal surface cracks.
If the self-healing of the surface crack which exists is carried out after an efficient machine operation is performed, then there is a great advantage in fabrication efficiency and fabrication cost.
Since all surface cracks are healed, reliability improves greatly.
It is advantageous if a crack which occurs while in service can be healed and full recovery of strength achieved.
From the above ideas, the self-crack-healing behaviors of ceramics were investigated by Ando and co-worker. Silicon nitride (Ando et al, 1998; Yao et al., 2001), alumina (Takahashi et al., 2003; Ando et al., 2004; Nakao et al., 2005a), and mullite (Chu et al., 1995; Nakao et al., 2006), SiC (Kim Y.W. et al., 2003; Lee et al., 2005a) and ZrO2 (Houjou et al., 2010), with the self–crack-healing ability have been developed. In the following section, an outline is given of the crack-healing behavior of ceramics.
2. Nano-composite and multi-composite
SiC particles of nano size are added to the material, preventing grain growth of the matrix in the sintering process, and improving the bending strength through grain refinement: For example, in the case of an alumina, bending strength can be increased from about 400 MPa to 700 ~ 1000 MPa (Ando et al., 2004).
SiC particles of nano size 15 to 30 vol% added to the material, and induce a self-crack-healing ability.
SiC particles of nano size are distributed not only in the grain boundaries of an alumina, but in individual grains and increases the heat-resistant limit by 300 K.
The fracture-surface photography of the Al2O3 nano-composite material is shown in Fig Most of the SiC particles were distributed uniformly in the grain boundaries; however, several nanosized SiC particles were distributed in the Al2O3 grain, as shown in Fig. 1 (Ando et al., 2004).
A multi-composite material is a material which combines nanosized SiC particles and SiC whiskers in the proportion of 25 to 30%, and has excellent self-crack-healing ability, fracture toughness, strength (Nakao et al., 2006, Takahashi et al., 2007). The proportion fraction of SiC particles to SiC whiskers is determined by taking into consideration the self-crack-healing ability and fracture toughness requirements. If the proportion fraction of SiC particles is increased, then the crack healing rate will be increased. If the proportion fraction of SiC whiskers is increased, then the fracture toughness will be improved (Nakao et al, 2005a).
The composition system of the ceramics used in this paper and the effective temperature ranges in which crack-healing is possible are shown in Table 1. The room-temperature bending strength and fracture toughness of the multi-composite ceramics are shown in Table 2.
Is has been common knowledge for many years that the strength of ceramics is improved by heat-treatment in air. This occurs by three mechanisms, as follows.
The crack-healing phenomena, which is explained in this paper.
Release of tensile residual-stress.
In case ii), the material must be heated to a nearly sintering temperature, which is a higher temperature than it is heated in the crack-healing phenomena (Lange et al., 1970; Kim et al., 2003). In case iii), the strength recovery rate is small and the crack still remains (Thompson et al., 1995).
The material with a self-crack-healing ability described in this paper has all of the following attributes.
The material itself detects an occurrence of a crack and begins crack-healing activities.
A crack causes a 50 ~ 90 % reduction in the strength of a material, but in material with a self-crack healing ability, the material heals the crack completely, and the strength of the material is completely recovered.
The strength of a crack-healed area is equivalent to or higher than that of a matrix area up to about 1673 K.
3. Nano-composite and multi-composite
3.1. Mechanism of crack healing
The crack healing of ceramics developed by the authors is caused by the following oxidation reaction of SiC.
From Eq.(1), it can easily be understood that a monolithic mullite or a monolithic alumina does not reveal a crack healing ability, since oxidization is saturated in these materials. A schematic diagram of the crack healing mechanism is shown in Fig 2. The following three conditions must be met for a crack-healed area to recover completely.
The volume between the crack walls must be completely filled with the products formed by the crack-healing reaction:
The strength of the crack-healing substance must be equivalent to or higher than that of the matrix:
There is a glass phase and a crystalline phase in SiO2 in Eq.(1). If the crack-healing material was crystal SiO2, then the crack-healed sample would exhibit high bending strength even at an elevated temperature. However, if the crack-healing material was glassy SiO2, then the crack-healed sample would exhibit low bending strength at an elevated temperature. A key point of crack-healing technology is how many crystalline phases are deposited in a crack-healing substance. The large exothermic heat of 943 kJ in Eq. (1) seems to satisfy this condition.
The crack healing substance must be strongly bonded to a matrix.
Bonding to a matrix is attained by the huge exothermic heat of 943 kJ by fusion and mixture of a matrix and a healing substance. How much nano size SiC should be added to the Al2O3 matrix in order to satisfy the three crack-healing conditions? We investigated the effect of the volume fraction of SiC on the crack-healing behavior of an Al2O3/SiC composite.
Figure 3 shows the experimental results. The crack introduced on the test specimen is a semi-elliptical crack 100 μm in surface length and 45 μm in depth (hereafter called a standard crack). The open circles show the fracture of the specimens initiated from outside the crack-healed zone, indicating that complete crack healing occurred. With respect to strength, the optimal volume fraction of SiC is 7.5 to 10 %. However, with respect to crack-healing ability, a volume fraction of SiC larger than 10 % is recommended. However, when the SiC additive rate exceeds 30%, the strength begins to vary greatly, since a SiC agglomeration is formed. On the other hand, a large crack can be healed with an increased SiC volume fraction. The authors recommend a standard SiC volume fraction of 15 ~ 30 %.
3.2. Oxygen partial pressure and temperature dependency of crack-healing behavior
We used three-point bending-test specimens as shown in Fig 4 to evaluate the bending strength (σB) of a crack-healed specimen. We introduced the standard crack into the central part of the test specimen. The decreasing rate of the strength by this crack was 50 to 85%, although it was greatly dependent on the fracture toughness of the material.
The influence of atmosphere on the crack-healing behavior of Al2O3/15 vol% SiC is shown in Fig 5 (Kim B.S. et al., 2003). The bending strengths (σB) of a as-received test specimen are about 650 MPa. When a standard crack was introduced into this specimen, the σB was reduced to 180MPa and the decreasing rate of σB was about 73 %. However, when the crack healing of this pre-cracked specimen was carried out in air at 1573K for 1 h, the bending strength (σB) was improved up to about 800 MPa. The σB of a crack-healed specimen is larger than the σB of a as-received specimen. The reason for this is because even minute cracks on the surface of the as-received specimens recovered completely. However, when the pre-cracked specimens were heated in a vacuum, N2 gas, and argon gas, the σB recovered to at most 350 MPa. The recovery of σB is insufficient. The slight increase of σB by this heat-treatment occurred because the tensile residual-stress of the crack tip was removed. Similar crack healing and strength recovery behaviors were reported in mullite (Chu et al., 1995), Al2O3 (Chou et al., 1998) and Si3N4 (Ando et al., 1998; Jung et al., 2008a). Figure 6 shows a specimen after the bending test. Fig 6 (a) shows the case of a pre-cracked specimen. The pre-cracked specimens fractured from the pre-crack division. In the case of Fig 6 (b), because a crack was healed completely, the crack was initiated from matrix division.
As described in section 3.1, crack healing is dependent on an oxidation reaction. Therefore, it is assumed that crack-healing behavior is greatly dependent on oxygen partial pressure. The influence of oxygen partial pressure on crack-healing behavior is shown in Fig 7, in Al2O3/SiC composite materials (Osada et al., 2009). When crack-healing was carried out at 1673K, in air (oxygen partial pressure: 21kPa), the crack healed completely in about 20 minutes. When the oxygen partial pressures were 5000 and 50 Pa, the crack healed completely in about 1 h and 70 h, respectively. Moreover, the test specimen which healed in thin oxygen showed a bending strength equivalent to a matrix division to 1673K. It is said that the oxygen partial pressure in the exhaust gas of a gas-turbine or a vehicle is about 8kPa-10kPa, which is approximately half in an atmosphere. So it is anticipated that the surface crack can be healed in oxygen partial pressure in the exhaust gas of a gas-turbine or a vehicle.
The influence of temperature on crack-healing behavior is shown in Fig 8 (Ando et al., 2009; Nakao et al., 2009). When the crack-healing times were 10 h and 300 h, the temperatures in which a crack was healed completely were about 1473 K and 1273 K, respectively. By conducting an experiment as shown in Fig 8 on various materials, we found the shortest time
The activation-energy (
3.3. Crack-length dependency of crack-healing behavior and strength
The crack-length dependency of a fracture stress or a crack-healing behavior is important. The crack-length dependency of a fracture stress or a crack-healing behavior obtained with Al2O3 strengthened with SiC whiskers is shown in Fig 10 (Nakao et al., 2005a). The crack-healing conditions are 1673K and 1h in air. The 2
4. High-temperature strength characteristic of crack-healed specimen
The temperature dependency of the bending strength (σB) of a crack-healed specimen is shown in Fig 11. Each test specimen was crack healed by an optimum condition after a standard crack was introduced. The heat resistance limit for the bending strength of Al2O3/SiC is about 300 K higher than that of monolithic Al2O3; this excellent increase in the heat resistance limit was attained by a nano-composite, as mentioned in section 2. The heat-resistant limit at the crack-healed division of the commercial SiC was 873K, much lower than that of the matrix division (Lee et al., 2005b). As shown in the figure, a new SiC, which has a heat-resistant limit of a crack-healed division of about 1673K, has been developed, and we examined its usage (Lee et al., 2005a). The heat-resistant limit of the silicon-nitride with Al2O3 added to it was about 1273K. The heat-resistant limit of the new silicon nitride which improves the composition system is about 1673K, which is higher than the heat-resistant limit of the silicon nitride with Al2O3 added. The large improvement in such a heat-resistant limit was attained by the crystallization of a grain boundary or a crack-healing substance. In addition, most test specimens fractured from the matrix division below to the heat-resistant limit temperature among the materials of Fig. 11, except the commercial SiC. This implied that the crack-healing division had sufficient bending strength.
5. Crack-healing behavior of machined specimens
In general, final machining processes such as polishing and lapping are performed to remove non-acceptable flaws. Although these processes are generally very costly, they cannot eliminate minute cracks. Moreover, even if final machining is adopted, a minute crack may remain, causing a reliability problem. It is anticipated that substituting the crack-healing process for the final machining processes leads to economical manufacturing of ceramic components with high reliability. The crack-healing behavior of machined specimens was investigated by several researchers (Lee et al., 2005c; Osada et al., 2007; Jung et al., 2008b). The experimental results showing the effects of crack-healing on increasing the reliability of machined components will be explained (Osada et al., 2007).
Machined Al2O3/20 vol.% SiC whiskers having a semicircular groove were used. The sintered plates were cut into 3 mm × 4 mm × 22 mm rectangular bar specimens. A semicircular groove was made at the center of the smooth specimens by using a diamond-coated ball-drill as shown in Fig. 12. The cut depth by one pass (
All fracture tests were performed on a three-point bending system with a span of 16 mm, as shown in Fig. 12. The crosshead speed was 0.5 mm/min. The tests were conducted at room temperature. The local fracture stresses (σLF) considering the stress concentration factor of the semicircular groove (α= 1.2) were evaluated.
Figure 13 shows the strength of the machined specimens with a semicircular groove as a function of the cut depth by one pass (
Therefore, it was concluded that crack healing could be an effective method for improving the structural integrity of machined alumina and reducing machining costs.
6. Crack-healing behavior during service
Ceramic components are often operated continuously under constant or cyclic loading at elevated temperatures under lower oxygen partial pressure. If a crack initiates during service, the component’s reliability will be considerably reduced. If the crack could be healed under even service conditions, and the healed zone had sufficient strength, the reliability and lifetime of ceramic components could be increased. The crack-healing behaviors under constant or cyclic stress have been systematically studied for Si3N4/SiC (Ando et al, 2002b; Takahahi et al., 2005), Mullite/SiC (Ando et al., 2001; Takahashi et al. 2007), Al2O3/SiC (Nakao et al., 2005b), and SiC (Lee et al., 2005a). Pre-cracks of 100 μm can be healed completely, even under constant or cyclic stress.
To take advantage of the crack-healing ability during service, it is essential to determine the threshold stress for crack-healing below which a crack can be completely healed. In this section, the critical stress condition for crack healing in Si3N4/SiC and other ceramics are shown.
6.1. Crack-healing behavior of Si3N4/SiC under stress and low oxygen pressure
The material studied was a hot-pressed SiC-particle reinforced Si3N4 that contained 20 wt% SiC particles and 8 wt% Y2O3 as a sintering additive. Semi-circular surface cracks of 100 μm in surface length were introduced at the center of the tensile surface of the bending test specimens using a Vickers indenter. After introduction of the pre-cracks, crack-healing tests under cyclic or constant stress were carried out. Figure 15 shows the crack-healing process. Crack-healing was carried out under cyclic (σmax, ap) or constant (σap) bending stresses at a healing temperature (
Figure 16 shows the results of the bending tests on specimens crack -healed at 1473K for 5h under constant stress in
Figure 17 shows the bending strength (σB) and cyclic fatigue limit (σf0) at the healing temperatures between 1173 K and 1473 K. The ratio of σf0/σB was 0.67 ~ 0.86 at each healing temperature (Takahashi et al., 2005). Therefore, it can be concluded that the cyclic fatigue limit was sufficiently high even at the healing temperature.
On the bottom of Fig. 15, the crack-healing behaviors under stress are indicated schematically (Takahashi et al., 2005). The change in the crack-length during crack-healing is divided into three cases, (I), (II) and (III). In process (I), slow crack growth from the pre-crack tip occurs and the cracks lead the specimen to failure because the crack growth rate is higher than the crack-healing process. In process (II), slow crack growth from the pre-crack tip also occurs. The crack-healing process starts at high temperature, the crack growth rate decreases due to crack-healing and finally the cracks are healed. In process (III), slow crack growth from the pre-crack does not occur, and thus the pre-cracks are easily healed.
In the case of crack-healing under the constant bending stress (σap) of 250 MPa and 300 MPa, the crack-healing behavior is classified into process (I) or (II). However, in the case of σap= 200 MPa, the crack-healing behavior is classified into process (III). The applied stresses are lower than the threshold stress for crack-healing and the pre-cracks were healed easily.
6.2. Threshold stress for crack-healing for Al2O3/SiC and Mullite/SiC
Figure 18 shows the threshold constant or cyclic stress for crack healing as a function of the bending strength of pre-cracked specimens (Nakao et al., 2007). Al2O3/15 vol% SiC particles (AS15P), Al2O3/15 vol% SiC whiskers (AS15W), mullite/15 vol% SiC particles (MS15P), and mullite/15 vol% SiC whiskers (MS15W) were tested. The closed and open symbols indicate the threshold constant and cyclic stresses, respectively. All data except that of MS15W are satisfied by the proportional relation in spite of the different crack-healing conditions. The proportional constants for the relationship between the threshold stress and bending strength of pre-cracked specimens is 64 % for constant stress and 76 % for cyclic stress.
7. A methodology to increase the structural integrity against embedded flaws
Oxygen is necessary for crack-healing, and thus embedded flaws such as pores and abnormally large grains cannot be healed. These facts suggest the importance of a proof test for higher reliability. However, engineering ceramics show nonlinear fracture behavior as shown in Fig. 19, and ceramics components are not used only at the proof-tested temperatures. Ando et al. have proposed a theory to evaluate the temperature dependence of a guaranteed (minimum) fracture stress of a proof-tested sample based on nonlinear fracture mechanics (Ando et al., 2002c). In this section, the theory and its application are explained.
The nonlinear fracture behavior is expressed very well by the process zone size failure criterion, as shown in Fig. 19 proposed by Ando et al (Ando et al., 1993). The criterion is expressed by eq. (3) as follows:
Figure 19 shows a schematic relationship between σC and
where σp R is the proof test stress at room temperature, and the superscript
where the superscript
Figure 20 shows the data on the fracture stress of the crack-healed and the proof-tested specimens as a function of temperature with the evaluated σG for the crack-healed alumina/20 vol% SiC particles composite when σp = 435 MPa (Ono et al., 2007). Except the data at 1373 K, all specimens have higher strength than the σG at all temperatures. Also, the minimum values of the experimental fracture stress are almost equal to the σG at all temperatures. At 1373 K. the σFmin is 6.8 % less than σG, but the value exists in the dispersion evaluated from the
Moreover, the guaranteed theory can be applied to Si3N4 (Ando et al., 2002b; Ando et al., 2005) and coil spring made of Si3N4 (Nakatani et al., 2005). The results obtained can be seen in Fig. 21, where the measured σFmin is plotted as a function of the evaluated σG.
8. Through life reliability of ceramic components
The flow chart of a new methodology to guarantee the structural integrity of a ceramic component is shown in Fig. 22. This new concept consisted of the following three stages:
crack-healing under optimized conditions,
proof testing, and
in-situ (in-service) crack-healing.
By machining, many surface cracks will be induced and reliability will decrease considerably. However, by crack-healing under optimized conditions, surface cracks can be healed completely and reliability will be increased.
However, for the crack-healing of the above ceramics, oxygen is necessary. Consequently an embedded flaw cannot be healed. This means that the structural integrity of ceramic components before service cannot be guaranteed only by crack-healing technology. A new theory to explain the temperature dependence of minimum fracture stress guaranteed based on non-linear fracture mechanics was proposed as mentioned in section 7. Thus, before service, the structural integrity of ceramic components can be confidently guaranteed using the concept: crack-healing + proof test.
After service, if a crack is initiated, structural integrity will decrease considerably depending on the crack size. However, if a material can heal a crack in service, it would be very desirable for structural integrity. As mentioned in section 6, several materials developed by the present authors can heal a crack during service. Thus, a new concept shown in Fig. 22 is effective to increase the through life reliability of ceramic components.
Structural ceramics are generally brittle, which seriously affects the reliability of ceramic components. Four methods are used to resolve this weakness:
the ceramic is toughened by fiber reinforcement or microstructural control,
high level non-destructive inspection and repair of the unacceptable flaws,
using the proof test and then only using the components that have high reliability, and
making use of the self–crack-healing ability. In this chapter, special attention was paid to method (d), the self–crack-healing ability of structural ceramics.
In Section 1, the advantages of using the crack-healing ability of ceramics are outlined. In Section 2, nano-composite and multi-composite materials having crack-healing ability are presented. In Section 3, basic crack-healing ability is introduced in detail. In Section 4, the high-temperature strength characteristics of crack-healed specimens are explained. Machining is a necessary process for ceramic machine components, but machining can cause many cracks in the components. In Section 5, it is explained in detail how the many cracks introduced by machining can be healed and strength recovered completely. If a material were able to heal a crack that initiated during its service, it would be extremely beneficial for the structural integrity of a ceramic component. Thus, in Section 6, crack-healing behavior under stress and the resultant strength at the temperature of the crack healing are introduced in detail. Even if all surface cracks were healed completely, embedded flaws such as cracks and pores cannot be healed, because oxygen is necessary for crack healing. Thus, a proof test is necessary for the higher reliability. In Section 7, a detailed explanation of the proof test theory and its usefulness is given. In Section 8, a methodology to increase the through life reliability of ceramic components is explained.
In conclusion, the crack-healing ability of structural ceramics is a very useful technology for higher structural integrity and for reducing the machining and non-destructive inspection costs.