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Vacancy migration energy is a key factor for irradiation resistance of nuclear materials and also a fundamental parameter for modeling and should be experimentally calculated in advance. A new method together with a formula was developed for measuring the vacancy migration energy on high-voltage electron microscope (HVEM) from the temperature dependence of the growth speed of a dislocation loop in consideration of other sink effects including surface and grain boundary on point defects. Anti-noise property and the other characteristics of the three different methods have also been analyzed and discussed to help choose the appropriate method to measure the vacancy migration energy when in need in different situations.
School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing, China
*Address all correspondence to: ppliu@ustb.edu.cn
1. Introduction
Fusion energy is one of the most promising carbon-free energy in the future. One problem limiting the development and application of fusion energy is the radiation damage of materials. Irradiation resistance of a material is determined by the motion and recombination of point defects (vacancy and interstitial) [1]. The motion and recombination of point defects are governed by the vacancy mobility at material service temperature which is always higher than the vacancy mobile temperature [1, 2]. Thus, vacancy migration energy is a critical factor for the ability of nuclear materials to resist radiation damage. Moreover, it is becoming a popular and an effective method to simulating the irradiation-induced microstructure changes to predict the mechanical properties of materials during irradiation with the development of computational materials. Vacancy migration energy is also a fundamental parameter for modeling and should be experimentally measured in advance.
Kiritani et al. have firstly proposed one method as early as the 1970s by experimentally measuring growth speed of interstitial dislocation loops at different irradiation temperatures to measure the motion of vacancies in iron by using HVEM [2, 3]. High-energy electron irradiation produces pure Frenkel point defect pairs, which is very beneficial to the fundamental research of point defect mobility. In combination with in situ heating sample holder, HVEM has been proven to be a powerful apparatus to investigate microstructural evolution and measure the vacancy migration energy under in situ high-energy electron irradiation. Since then, the method proposed by Kiritani et al. was often used to measure the vacancy migration energy of materials. The effects of impurities, helium, and hydrogen on vacancy migration energy in pure Fe-based alloys, F82H and electron-beam-welded F82H joint, have been investigated by Hashimoto et al. [4, 5, 6]. The effect of deuterium on vacancy migration energy in Fe-10Cr alloy has also been investigated [7]. Point defect behavior in pure vanadium and its alloys were also analyzed under HVEM irradiation by using the method [8, 9, 10]. However, it is important to note that the method did not consider the effect of sample surface on the measurement of the vacancy migration energy. And, it is always very difficult to ensure that the observed loops are deep in the specimen (located so far apart from specimen surface) by HVEM stereo observation operation [11]. Thus, Wan et al. derived a new formula for calculation vacancy migration energy by considering the surface effect in the 1990s [11]. In this brilliant derivation, the effect of specimen surface was treated as a constant, and three data of growth rate at different irradiation temperatures were used once to numerically calculate the vacancy migration energy by iterated operation. This method considered the surface effect intrinsically, but iterated solution by using a computer is needed. This operation would produce two roots, in which one should choose the right one according to physical meaning. It is a little bit difficult to calculate and choose the right root. Probably for this reason, reference of using this numerical method is not many. Moreover, the effects of other sinks such as irradiation-induced small void, fine precipitates, and grain boundary on the growth speed of dislocation loops also needed to be considered when using HVEM to measure the vacancy migration energy.
In this chapter, other sinks such as surface, small void, precipitates, and grain boundary were taken into consideration to develop a new method for calculating vacancy migration energy according to the relationship of the reciprocal of irradiation temperature and growth speed of dislocation loops. An influential factor relating to the effects of other sinks was also presented in this new method. In addition, the formula derived by Wan et al. has also been rediscussed to avoid one root and help to choose the right root, which may encourage a broader range of applications of this numerical method. The characteristic of these three methods is discussed to help choose the appropriate method to measure the vacancy migration energy when in need in different situations. In addition, the motion interstitial is also important and could be measured by using HVEM [12, 13]. In this chapter, however, we only discussed the mobility of vacancy because vacancy moves much slower than that of interstitial, and the recombination of vacancies and interstitial defects is governed by the vacancy mobility at material service temperature which is higher than vacancy mobile temperature.
This method was reported by Kiritani et al. [2] and Tabata et al. [14] in which several factors affecting the migration energy were discussed in detail. According to their analysis, the variations of the concentrations of interstitial atoms (Ci) and lattice vacancies (Cv) with the point defect mobility (M) at high temperature (at which vacancies are highly mobile) are given as follows:
dCidt=P−ZivMi+MvCiCv−ZiLMiCsLCi−MiCsiCiE1
and
dCvdt=P−ZivMi+MvCiCv−ZvLMvCsLCv−MvCsvCvE2
where Ziv, ZL, and Cs denote the recombination coefficient, the number of reaction sites of dislocation loops and point defects, and concentration of sinks, respectively. And, t denotes the time. First term P is the production rate of free Frenkel pairs induced by HVEM. The second term is the mutual annihilation rate between interstitials and vacancies with the mutual annihilation cross-section of Ziv. The third terms are the annihilation rate of each kind of point defect to dislocation loops whose concentration of atomic sites as sinks is CsL and with absorption cross-sections ZiL and ZvL at each site for each point defect. The last terms are the annihilation at the surface sink. When a steady state of point defect concentrations is established, there is:
dCidt=dCvdt=0E3
Then, both Eqs. (1) and (2) are equal to zero, and one can obtain the following equation:
ZiLCsL+CsiMiCi=ZvLCsL+CsvMvCvE4
The most dominant terms of the point defect annihilation are the second terms in Eqs. (1) and (2), at least for the “thick-foil” case in which the last terms in the equations never become dominant. Then one can obtain the following, under the condition of Mi ≫ Mv:
P=ZivMiCiCvE5
Using Eqs. (4) and (5), the following equation could be obtained:
MvCv=βMiCi=βPZivCv=βPMvZivE6
where β = (ZiLCsL + Csi)/(ZvLCsL + Csv). Since Csi and Csv are considered to be equal to each other and stay constant as long as the loop remains at the same fixed position in a specimen foil, the value β is thought to be slightly larger than unity because of the slightly larger capture cross-section ZiL for interstitial than that for vacancy, ZvL, at a dislocation loop and can be taken as constant (at least at a fixed temperature) though it varies slowly with the increase of CsL by the growth of the dislocation loops [2].
The growth speed of interstitial loop of size R is expressed by the arrival rate to the loop of interstitial atoms in excess of vacancies and is:
dRdt=aZiLMiCi−ZvLMvCv=aZiLβ−βZvLzivPMvE7
where a is the increase of loop size by the absorption of one point defect per one site on the dislocation [2]. ZiLMiCi and ZvLMvCv are the ensemble of point defect fluxes captured by the loop. In order to reduce the effect of loop’s size, the loops with same/similar initial size should be selected during experimental operation, which can be done relatively easily. Then, the equation can be written as:
dRdt=C·exp−Emv2kTE8
where k is the Boltzmann constant and C is an experimental constant. The above equation can be rewritten as:
lndRdt=lnC−Emv2kTE9
Using this equation, the vacancy migration energy can therefore be obtained from the slope of a linear relationship between the logarithm of the growth rate of dislocation loops and the inverse of temperature. Here, we called this method “linear method.”
2.2 Numerical method
Using the “linear method” with Eq. (9), the vacancy migration energy can be calculated simply. However, the position of the dislocation loop must be deep in the thick foil to ensure the surface effect could be avoided. This makes the experiment more complex and difficult. Considering the surface effect of the sample, another brilliant derivation was developed by not avoiding the third and fourth terms of Eqs. (1) and (2) by Wan et al. [11].
When the point defect concentration is in a steady state, there is dCi/dt = dCv/dt = 0. And one can obtain an equation under the condition of Mi ≫ Mv:
where A2 and B2 are constant. This equation can be changed to be:
expEmkTdRdt2−B3dRdt−A3=0E14
Letting dR/dt = V, the above equation can be expressed as:
expEmkTV2−B3V−A3=0E15
By HVEM observation, V1, V2, and V3 at temperatures T1, T2, and T3 can be obtained, respectively. Using these data in Eq. (15) and getting rid of the constant, there is:
and where k is the Boltzmann constant. Eq. (17) can be solved by using a computer. A Python program example for solving Eq. (17) is given in the Appendix. According to Eq. (17), two mathematical results would be obtained. In this case it is necessary to select one of these two results by the physical meaning. Sometimes, one will have a little difficulty in choosing the correct result. Probably for this reason, the application of this method had been limited.
The derivation was discussed here again to help select the result of Eq. (17). Two roots were induced by the Eq. (11) firstly. We can avoid one root directly in Eq. (12) by the physical meaning:
2A1Cv>0
where A1 = Ziv/β > 0, Cv is the concentration of the vacancy. So, Eq. (12) could be rewritten as:
There should be only one root for Em in the Eq. (15) in which A3 and B3 are constant. Thus, one knows to choose the big one of the two results from Eq. (17). Only one result will be obtained. This may encourage a broader range of applications of this method as it considers the surface effect intrinsically. We called this method “numerical method” here because of numerical calculating of the vacancy migration energy by iterated operation [15].
2.3 Nonlinear method
Using linear method, the vacancy migration energy could be obtained simply with no consideration of the surface effect. In order to ensure the surface effect could be avoided, however, the position of the dislocation loop must be deep which is difficult sometimes and will make the HVEM experiment more complex. Considering other sink effects such as surface, small void, precipitates, and grain boundary, some terms were added in Eqs. (1) and (2):
where Ziv, ZL, and Cs denote the recombination coefficient, the number of reaction sites of dislocation loops, and point defects and density of sinks, respectively. The first term P is the production rate of free Frenkel pairs induced by HVEM. The second term is the mutual annihilation between interstitials and vacancies. The third terms are the annihilation rate of each kind of point defect to dislocation loops whose concentration of atomic sites as sinks is CsL and with absorption cross-sections ZiL and ZvL at each site for each point defect. The fourth, fifth, and sixth terms are the ensemble of annihilation of each kind of point defect to void, precipitates, and grain boundary, respectively. It is worth noting that these three kinds of sinks mean a very small one or inconspicuous one which could not be observed by HVTEM at the same magnification times as observing the whole loop. One can avoid it directly during the TEM observation if the void or precipitates are big enough, which will not be discussed here. The seventh terms express the escape of point defects to the surface sink. Under the condition of Mi >> Mv and the steady state of point defect concentrations (dCidt=dCvdt=0), Eqs. (20) and (21) can be written as:
Set a1=Zivβ and b1=ZvLCsL+ZvoCso+ZvPCsP+ZvBCsB+Csv. According to the physical meaning, a1 and b1 are constant larger than zero. The above equation can be written as:
According to the physical meaning, MvCv should be larger than zero, while −b1−b12+4Pa1MvMv2a1 < 0. Anyway, substituting Eq. (25) into Eq. (7), the following equation can be obtained:
drdt=aZiLβ−ZvLMvCv=b2±b22+a2MvMvE26
where a is the change of loop radius by the absorption of one point defect per one site on the dislocation [2].
ZiLβ−ZvL≈ZiL−ZvL=Lbias, thus, a2=a2PLbias2a1 and b2=−b1aLbias2a1.
where a3 = 1/4a2, b3 = b2. The above equation can be written as:
expEmkT=a3dtdr2+b3dtdrE28
As a3, b3 and b324a3=b22a2=b124Pa1 are constant. There is a constant d to hold the following equation:
d∗expEmkT=a3dtdr+b32a32E29
From the above equation, one can obtain:
1T=2kEm∗lndtdr+B1+C1E30
where B1 = b3/2a3 and C1 is constant. By HVEM observation and getting dt/dr [1/(dr/dt)] data at different temperatures, the Em can be obtained by this equation. In order to plot easily, the equation can be rewritten as:
1000T=A∗ln1dr/dt+B+CE31
Note: A = 2 k*1000/Em, B = −b1/(a*P) is a negative constant relating to total effects of all other sinks. Thus, from the function of 1/(dr/dt) and 1/T, the Em can be obtained by plotting the curve according to Eq. (31).
Measurement of vacancy motion in solid state materials is a challenging work. There are not so many experimental methods. In situ HVEM has been proven to be one of the powerful tools to obtain vacancy migration energy by measuring the temperature dependence of the growth speed of a dislocation loop during electron irradiation. A reasonable phenomenological model of the loop growth could be selected and applied to extract the vacancy migration energy from the experimental data. Kiritani et al. firstly proposed one linear model to calculate the vacancy migration energy. Then, Wan et al. derived a new formula by considering the surface effect. In this chapter, a new nonlinear model was developed by considering the other sink effects such as surface, small void, small precipitates, and grain boundary, and the numerical method was rediscussed. When the measured experimental data are ideal, not affected by the surface or other defect sinks, the vacancy migration energy value calculated by the three methods should be the same. One experimental example for calculating the vacancy migration energy by using the three methods was given here. The sample was Fe-10Cr model alloy which was pre-implanted by He and H ion sequentially. Then electron irradiation and in situ observation were carried out in HVEM at 573, 673, and 773 K. At a corresponding temperature, the growth rates of dislocation loop were measured [15]. But, the ln(dR/dt) and 1/T calculated from the experimental data were not strict linear that means there may be influences from the sample surface or other sinks. Thus, three assumed ideal values of the growth rate which are close to the three experimental values were selected to test the three methods, which are about 1.1 nm/min at 573 K, 3.5 nm/min at 673 K, and 8.1 nm/min at 773 K, respectively. According to these values, the ln(dR/dt) and 1/T followed a strict linear relationship, which means an ideal situation without the effect of other sinks. Then, the three methods were used to calculate the vacancy migration energy in this ideal case, and the results were shown in Figure 1. Figure 1(a) showed the result calculated by the linear method where blue squares are the experimental data and red pentagrams are the ideal values. The result calculated by the numerical method was shown in Figure 1(b); the solving process example of the Eq. (17) was given in the Appendix. Figure 1(c) showed the result calculated by the nonlinear method where the horizontal axis represents the inverse of the growth rate and the vertical axis represents the inverse of temperature. These results indicated that the vacancy migration energy value calculated by the three methods according to ideal values in He+H pre-implanted Fe-10Cr sample was the same which was about 1.52 eV, while the vacancy migration energy values calculated by a different method according to the experimental data were different because of the different characteristics of the method. The characteristics of three methods for measuring vacancy migration energy were listed in Table 1.
Figure 1.
Measurement of vacancy migration energy in sequential-(He+H) ion implanted Fe-10Cr samples according to the ideal values by using linear method (a), numerical method (b), and nonlinear method (c), respectively.
Methods
Considering surface effect
Considering other sinks effect
Anti-noise property
Linear method
No
No
Very good
Numerical method
Yes
No
—
Nonlinear method
Yes
Yes
Good
Table 1.
The characteristics of three methods for measuring vacancy migration energy.
In addition, if the linear fitting degree is larger than 0.9 which means the effect of other sinks was not dominated, linear model was preferred to fitting the experimental data and obtaining the value of vacancy migration energy because it is very simple. Otherwise, nonlinear model or numerical method should be used in considering the surface effect and other sink effect intrinsically. And, the overall influence of other sinks was also given as an influence factor (B) in the nonlinear model. It is worth to note that the “nonlinear method” has one more parameter than “linear method,” which means there is a bigger possibility for overfitting problem to arise. Thus, one should notice that parameter B should be negative according to Eq. (31) to avoid the overfitting problem. Another thing which needs to be noted is that Mi >> Mv is appropriate for pure metals, but Mv > Mi may exist for some alloys [11, 16, 17]. The anti-noise property and the result reliability of different methods were also discussed in Ref. [18] and listed in Table 1. Then, one can choose an appropriate method to measure the vacancy migration energy according to the anti-noise property, result reliability, and other characteristics of the three different methods.
In summary, the methods to measure the vacancy migration energy by using HVEM were described and discussed in this chapter. Considering other sinks effects, a new nonlinear method was developed to measure vacancy migration energy according to the relationship of the reciprocal of irradiation temperature and growth speed of dislocation loops. Meanwhile, an influential factor relating to the effects of other sinks was also presented. The characteristics of three methods for measuring vacancy migration energy were also discussed in detail, which can help to select the appropriate method to measure the vacancy migration energy in different situations.
This work is supported by the National Natural Science Foundation of China (Grant Nos. 51601012, U1637210, 11775018, 51571021). The authors gratefully acknowledge the HVEM laboratory in Hokkaido University, Japan. The help and suggestions from Professor Q. Zhan and F.R. Wan at University of Science and Technology Beijing and Professor S. Ohnuki at Hokkaido University were highly appreciated.
Python program example (He+H implanted sample for example) for solving Eq. (17) is given here. Two methods were tried to solve Eq. (17). One is Newton iteration method and another is directly plotting the curve. Here we paste the program to illustrate the solving of Eq. (17) by directly plotting, which may be the simplest and most effective method. #Python 3.6 #Filename: Cal Em by using Numerical Method plot curve of Em import numpy as np import pandas as pd import matplotlib.pyplot as plt print('- - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - -') print('Import the growth rate data of He+H implantation…') (t,v)=np.loadtxt('.\\loop growth rate_He+H.txt', skiprows=1, unpack=True) print('T(K)',' V(nm/min)') print(t[0],v[0]) print(t[1],v[1]) print(t[2],v[2]) v0=(v[0]-v[1])/(v[1]-v[2]) v0=float('%.5f'%v0) print('\nV0 is:',v0) a1=(v[0]*v[0])/((1+v0)*v[1]*v[1]) a1=float('%.5f'%a1) a2=(v0*v[2]*v[2])/((1+v0)*v[1]*v[1]) a2=float('%.5f'%a2) b1=100000*(1/t[0]-1/t[1])/8.6 b1=float('%.5f'%b1) b2=100000*(1/t[2]-1/t[1])/8.6 b2=float('%.5f'%b2) print('\ny=a1*exp(E*b1)+a2*exp(E*b2)-1') print('a1 ','b1 ','a2 ','b2') print(a1,b1,a2,b2) #Plotting of Em of He+H-implanted sample x=np.arange(0,1.1,0.000005) #y=a1*exp(x*b1)+a2*exp(x*b2)-1, is not available here, use y=y1+y2 y1=a1*np.exp(x*b1) y2=a2*np.exp(x*b2)-1 y=y1+y2 i=len(x)-1 while y[i]>0.00001: i=i-1 else: print('Em:',2*x[i]) #M. Kiritani, H. Takata, K. Moriyama, et al., Philos. Mag. A, 40 (1979) 779-802. print('y:',y[i]) He+H_data={'y=a1*exp(x*b1)+a2*exp(x*b2)-1':y, 'Em':x} df1=pd.DataFrame(He+H_data) df1.to_csv('.\\He+H_data.csv') plot1=plt.plot(x,y,'r',label='He+H implanted') plt.xlabel('E') plt.ylabel('y in the equation') plt.legend(loc=2) plt.show() plt.savefig('p1.png')
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Written By
Pingping Liu
Submitted: 09 May 2019Reviewed: 29 May 2019Published: 26 June 2019
Open access peer-reviewed chapter
