The EIFS-based fatigue life prediction approach of nickel-based single crystals with film cooling holes at elevated temperature
Introduction
With the increasing performance requirements of modern aeroengines, turbine blades, which are their most critical components, are subjected to extremely high temperatures, necessitating the accurate prediction of the service life of the film cooling holes (FCHs) structure. Predicting the strength life of the different manufacturing and casting of nickel-base single crystal (SX) has always been an urgent problem to be solved in the engineering field [1], [2].
In the past few decades, researchers have focused on the study of material constitutive and the simple fatigue and creep of SX materials, such as the kinetic-constitutive approach [3] and crystallographic time-dependent damage models [4], [5], to characterize the evolution of damage-rates related to current physical quantities, such as stress, strain, strain rate, and material defects [6]. These models were studied prior to the occurrence of cracks. Crack propagation based on these mechanical mechanisms (such as energy density) has also been studied, but it has not been involved in structural parts [7], [8]. Leidermark et al. [9] and Bourbita et al. [10] used the critical distances method to predict the low-cycle fatigue life of SX-notched specimens, and achieved satisfactory results. However, two key problems for SX superalloys have not yet been solved: that is, the inaccurate anisotropic constitutive model and complicated fatigue damage mechanism and accumulation criterion of FCHs.
From another perspective, fatigue failure is historically characterized by crack initiation followed by crack propagation analysis, and the current prediction methods of fatigue life does not separate these two stages, because their boundaries are very difficult to determine. Although some scholars [11] regard different scale lengths of crack propagation as their boundaries, this is not accepted by most researchers. In addition, the crack growth path and growth rate of SX superalloys have obvious differences at different crack lengths [12], as shown in Fig. 1(a). Previous short-crack growth studies [13], [14] on SX superalloys reported that the nucleation and growth of cracks are closely related to the crystal orientation, loading, and temperature. The driving force of crack growth cannot simply be determined based on the stress intensity determined by using the conventional linear elastic fracture mechanics (LEFM), even though the crack growth life can capture the FCGR on the basis of , in conjunction with the Paris law [15], [16]. These models are often described by damage parameters, such as maximum plastic strain and maximum resolved shear stress [15], [17]; however, these studies can only explain the result of single factor or limited factor coupling, and the actual fatigue failure mostly starts from micro-defects, such as micro-cracks in the recast layer, micro-pores (∼10−6 m) of materials, etc. Furthermore, SX materials show different fracture modes at different temperatures and crystal orientations, usually mode I perpendicular to the loading axis and mixed crack propagation along the crystal surface [18], which further increases the difficulty of description.
An effective approach for estimating the fatigue life is the concept of equivalent initial flaw size (EIFS), which bypasses the above difficulties. The EIFS is not an actual defect size, but an “imaginary” defect size. The same fatigue life can be obtained by integrating the FCGR of long cracks (or approximate long cracks) at a point, as shown in Fig. 1(b). Once inferred, other similar structures under similar load conditions provide accurate estimates to avoid overengineering of the structure using EIFS values, comparable to a probabilistic fatigue life prediction model [22]. At present, the calculation of EIFS mainly focuses on the back-extrapolation theories, such as the TTCI theory [23], EPS method [24], and Bayesian updating [25], which are mainly calculated according to the recorded test data (such as fracture analysis, a-N curve) or the finite element (FE) method. Their calculation results have been proven in steel, aluminum alloys, titanium alloys, and other materials for standard smooth or notched specimens [26], [27], [28]. Unfortunately, their research mainly focuses on isotropic materials that the crack-growth morphology and path of these materials are significantly different from those of anisotropic materials. In addition, most of the calculated results of EIFS value are deduced according to the real fatigue life. A typical approach involves selecting a series of EIFS values and numerically evaluating their corresponding fatigue life, which are which are then compared with the experimental results; the most appropriate value amongst those in the series is the designated EIFS value [29]. The inferred EIFS value is closely related to the structure and test environment; therefore, it is impossible to further predict the fatigue life in other environments.
In recent years, the research teams have adopted purely deterministic methods to estimate EIFS in anisotropic materials, including the previously mentioned back-extrapolation method [30] and Kitagawa-Takahashi (K-T) diagram method [31], [32]. This method was first applied to isotropic smooth specimens and then transferred to notched specimens [33], [34], Li et al. [35], [36] further developed the EIFS into an SX FCHs structure. There was no doubt that the single EIFS value determined by the conventional K-T diagram was not sufficient. It was necessary to obtain the EIFS distribution (EIFSD) representing the uncertainty of EIFS that can reflect the original quality of a batch of samples or even other similar structures. Salemi et al. [25] proposed a method combining Bayesian and FE to estimate EIFSD with uncertainty and predict the fatigue life. Aliabadi et al. [37], [38] devoted themselves to solving for EIFSD using the double boundary element method combined with Bayesian. However, the accuracy of their results at high temperatures needs to be further verified, and the description of the FCGR for SX materials also needs to be further improved, because simple crack simulation modeling has a higher uncertainty than that of more traditional isotropic materials. Therefore, this study aims to expand the author's previous work through numerous tests, and develop an EIFS analysis method for the structure of SX FCHs at elevated temperatures, and predict the entire fatigue life on this basis.
The aims of this article are threefold: (i) to present a properties-driven probabilistic framework to predict the EIFS; (ii) to propose a crack initiation mechanism and propagation driving force for SX superalloy FCGR based on EIFS; and (iii) to verify the correctness of EIFS through surface integrity analysis and predict the total fatigue life. The remainder of this paper is organized as follows. Section 2 outlines a new EIFS determination method and life prediction framework for SX FCHs structures. Subsequently, the test results are analyzed to determine the crack initiation mechanism and develop a crack driving force considering the crack growth path in Section 4. Finally, Section 5 compares the EIFS results calculated using different methods, and performs surface integrity verification for EIFS and fatigue life prediction.
Section snippets
Method
The nucleation and propagation of cracks can generally be described according to Griffith’s condition and the relationship between the crack size and the required stress is given by Eq. (1) [39], where and are the elastic modulus and surface energy, respectively.
In Fig. 2(a), the Griffith line generally bends to satisfy the fracture stress of the finite specimen, which was revealed by El-Haddad et al. [40] for finite plate, which included an arbitrary addition
Material and specimens
The test material was an SX superalloy subjected to standard heat treatment, that process is: 1290 ℃× 1 h + 1300 ℃× 2 h + 1315 ℃× 4 h/AC + 1120 ℃×4h/AC + 870 ℃× 32 h/AC, and its nominal chemical composition is listed in Table 1 in detail. This material is mainly composed of blocky strengthening phase (γ' phase) and stripe matrix phase (γ phase), two-phase microstructure of the material is the ordered face-centered cubic (FCC) intermetallic compound Ni3Al. To ensure the same primary orientation
Fatigue crack paths and initiation mechanism
Fig. 5 shows the three-dimensional morphologies of Plates 1 and 2 after fractures at different temperatures. At high temperatures, owing the thermal activation process, the plastic deformation is not limited to the slip zone, and the initial fracture path presents a typical Mode I perpendicular to the loading direction. It may be noted that the lengths of the front and back cracks along the thickness direction are not the same, causing the transition to the crystal plane oblique crack
Determination of two stress intensity factor thresholds
It is generally difficult to determine the threshold for long cracks through structural components in high temperature environments. A dislocation at an angle to the slip direction at a distance from the crack tip (Fig. 9(a)). The dislocation movement rate is under shear stress , and the maximum force to promote crack propagation is generally either the external force or mirror force , while the other forces resulting from the surface energy are ignored [59]. The expressions of
Conclusion
The current study has carried out a large number of SX FCHs fatigue tests of two drilling processes (EDM and LDM) at different temperatures. A fatigue framework based on surface integrity quantification from RT to high temperatures was developed, which took into account I) the original surface quality of FCHs can be regarded as the “mathematical” crack length, which meets a probability distribution, and II) the original surface quality at RT can directly correspond to the original state at high
Declaration of Competing Interest
The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
Acknowledgement
The research was supported by the National Natural Science Foundation of China (NO. 51875461, 51875462, 52105147), National Science and Technology Major Project (2017-IV-0003-0040, 2017-V-0003-0052, J2019-IV-0011-0079), the Natural Science Basic Research Plan in Shaanxi Province of China (2020JC-16), and Innovation Foundation for Doctor Dissertation of Northwestern Polytechnical University (No. CX2021068).
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