The current research of nuclear control rod drive mechanism (CRDM) movable latch only makes a simple measurement of wear mass. The wear volume and difference in various claw surfaces are ignored and the degradation mechanism of each claw surface is not clear. In this paper, a detailed degradation analysis was carried out on each claw surface of movable latch combined with wear result and worn morphology. Results indicate that the boundary of carbide is preferred for corrosion because carbide presents a nobler Volta potential compared to the metal matrix or boundary region. Due to the oscillation of drive shaft between the claw surfaces of movable latch, the dominant wear mechanism on the upper surface of claw (USC) and lower surface of claw (LSC) is plastic deformation caused by impact wear. Mechanical impact wear will cause the fragmentation of carbides because of the high hardness and low ductility of carbides. Corrosion promotes the broken carbides to fall off from the metal matrix. The generated fine carbides (abrasive particles) cause extra abrasive wear on USC when the movable brings the drive shaft upward or downward. As a result, USC has a higher wear volume than LSC. This research proposes a method to evaluate the wear on the whole movable latches using a 3D full-size scanner.
1 Introduction
The control rod drive mechanism (CRDM) is located inside the nuclear pressure vessel, which drives the neutron absorption control rod to move up and down, keeps at the commanding height, and drops when the power is off, thereby completing the reactor startup, power adjustment, and safe shutdown [1, 2]. Nowadays, magnetic lifting CRDM is widely used in a pressurized water reactor. The movable latch, as the key component of magnetic lifting CRDM, is responsible for driving the neutron absorption control rod. The neutron absorption control rod is installed under the drive shaft. The movable latch directly contacts and impacts the drive shaft, resulting in the tribocorrosion on the movable latch surface in high temperature water [3, 4].
Excessive wear of the latch will affect the action process of CRDM, leading to the occurrence of failure. In general, the Co-based alloy is widely used in nuclear power plant because of its excellent wear resistance and corrosion resistance [5]. The Co element becomes a radioactive source after irradiation and causes radiation damage to materials. Content of Co element is strictly controlled in the nuclear power plant. The movable latch is made of stainless steel substrate and Co-based alloy surfacing layer to improve the service life of CRDM [6]. Besides, C and Cr elements are added to the surfacing layer for enhancement of hardness and corrosion, respectively [7, 8].
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In recent years, numerous studies have been carried out on Co-based alloy. Krell et al. [9] reported the sliding wear behavior on various Co-based alloys at an elevated temperature and found that the morphology and distribution of carbides had a greater relationship with wear behavior. Nevertheless, the presence of carbides also affects corrosion behavior, especially on the initiation of localized corrosion or dissolution [10]. The carbides in Co-based alloy provide a desirable strengthening technology for wear resistance. However, the boundary of carbides is the preferred location for corrosion due to the Cr depletion at their boundaries [11‐13]. The claw surface suffers from the influence of tribocorrosion (the combined action of mechanical wear and corrosion) when the movable latch is exposed to a corrosive environment such as high temperature water [14]. This behavior is no longer a simple superposition of wear and corrosion but a synergistic effect [15]. Wear will cause damage to the passive film and promote corrosion. The generated passive film acts as boundary lubrication to reduce friction and wear [16‐18]. Brownlie et al. [19] suggested that wear is the dominant degradation mechanism of the Co-based alloy in the 3.5% NaCl aqueous solution. Wang et al. [20] reported the tribocorrosion behavior on Co-based alloy and found that the fine carbides were broken from the matrix due to the preferred corrosion at the carbides boundary, resulting in abrasive wear. Considering that the movable latch suffers from tribocorrosion behavior, it is necessary to carry out the degradation analysis on the latch surface.
This work is aimed to investigate the wear mechanism of movable latch after 6.5 million steps in high temperature water. A non-contact scanner was used to quantitatively evaluate the wear conditions on each claw surface. Then, the worn morphology was combined with wear results to reveal the degradation mechanism on various claw surfaces.
2 Structural Characteristics of the Movable Latch Assembly
CRDM was fixed above the nuclear reactor core, which drove the movable neutron absorption control rod to move up and down. The main structure of movable latch assemble was composed of lift coil, lift pole, lift armature, movable latch, and drive shaft, as shown in Figure 1. The lift coil was isolated outside the sealed shell and generated a magnetic field after receiving specified instructions. Then, the lift pole attracted the lift armature to move upward. As the movable latch was installed on the lifting armature, the drive shaft moved upward with the movable latch when the lift armature moved upward [21]. The lift armature, movable latch, and drive shaft moved downward under the action of gravity when the lift coil was switched off.
Figure 1
The main structure of movable latch assembly
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In this process, the movable latch moved a certain distance with the drive shaft and then stopped when it reached a specified position. Due to the gap between drive shaft and movable latch, the drive shaft oscillated several times between upper surface of claw (USC) and lower surface of claw (LSC) because of inertia effect. The movable latch surface was prone to damage in contact with the drive shaft in high temperature water.
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3 Experimental Scheme
To simulate the actual condition of CRDM, the movable latch operated 6.5 million steps in high temperature reactor vessel, which satisfied the design life requirements of 6 million steps [22, 23], as shown in Figure 2. The water temperature and pressure were 300 °C and 15.5 MPa, respectively. The Stellite 6 alloy surfacing layer deposited on austenitic stainless steel substrate was chosen as the sample of movable latch in this work.
Figure 2
Experimental tester for movable latch in high temperature water
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Microhardness was measured by a hardness-tester (DHV-1000ZTEST) with a holding time of 10 s and load of 500 g, and the results were shown in Figure 3. Microhardness of substrate was within 179 HV0.5 to 200 HV0.5. The scope of surfacing layer was between 455 HV0.5 and 485 HV0.5. The microhardness of fusion line between surfacing layer and substrate was equal to 256 HV0.5 approximately. The hardness of surfacing layer was 2.5 times that of substrate. The large error bar within the surfacing layer revealed the difference in hardness of various microstructures.
Figure 3
Microhardness from substrate to surfacing layer
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After the experiment, the untreated sample and sample after 6.5 million steps were sprayed developer and scanned with a noncontact 3D full-size scanner (OKIO-3M-100), as shown in Figure 4a. The model in Figure 4b was obtained using reverse engineering software. The model was segmented and extracted to obtain the wear results including profile, width, depth, area, and volume in various regions. No obvious stress exists on the side of pinhole, which was also composed of Stellite 6 alloy surfacing layer. This region was utilized to analyze corrosion behavior in high temperature water. Accordingly, as shown in Figure 4c, the movable latch was divided into five regions: the claw surfaces (Regions A, B, C, and D) and the side of pinhole (Region E). The movable latch was cut into blocks using wire cutting for better analysis in various regions.
Figure 4
Schematic diagram of degradation mechanism analysis for movable latch
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The surface and cross-sectional morphologies were analyzed with an optical microscope (OM; VHX-7000) and scanning electron microscope (SEM; JSM 7800F) to clarify the degradation mechanism in various regions. X-ray spectroscopy (EDX) and nano-indentation were applied to deeply analyze the microstructure of the precipitates and metal matrix.
4 Experimental Results and Analysis
4.1 Microstructural Characterization
Figure 5 shows the microstructure inside the surfacing layer. The growth of dendrite crystal has a certain orientation but no definite direction. The distribution of precipitate (dark particle) and metal matrix (bright region) was displayed through SEM at higher magnification. The large island-like and relatively small dot-scope precipitates are randomly segregated in the grain interior, showing inhomogeneous structures. The chemical composition of precipitate (Point A) and metal matrix (Point B) determined by the point mode EDX technique and is illustrated in Table 1. Results indicate that the precipitates are in rich Cr element, wherein the metal matrix has a relatively low content of Cr element. Meanwhile, the content of C elements within metal matrix is lower than that in the precipitate.
Figure 5
Microstructure of Co-based alloy surfacing layer
Table 1
Chemical composition of precipitate and metal matrix (mass fraction, %)
Element
Co
Cr
Fe
C
Ni
W
Si
Point A
14.2
68.5
0.0
11.8
0.0
3.0
0.0
Point B
60.1
19.4
6.8
4.5
3.6
2.8
1.8
×
The EDX line scanning result from precipitate to the metal matrix is shown in Figure 6. Same as the point mode EDX results, the dark particles are Cr-rich carbides and the metal matrix is Co-based alloy. At the boundary of carbide, the content of the Cr element declines slowly to the content similar to metal matrix, and this distance is approximately 0.44 μm. This situation is consistent with the studies that the formation of carbides depletes the Cr element at its boundaries [10‐13, 24].
Figure 6
EDX element line from precipitate to metal matrix
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Results in Figure 3 present the difference in hardness of various microstructures. The hard phase causes strong dispersion hardening within metal matrix [9]. Accordingly, in Figure 7, the nanoindentation experiment is performed on precipitate and metal matrix. In Figure 7a, the maximum depth of metal matrix is deeper than that of precipitate under the same load, which means that the nanohardness of precipitate is higher. The calculated results of nanohardness and elastic modulus in precipitate and metal matrix are shown in Figure 7b. The nanohardness values of precipitate and metal matrix are 15.78 and 5.63 GPa, respectively. The elastic modulus values of precipitate and metal matrix are 212.96 and 180.63 GPa, respectively. Compared to the metal matrix, the nanohardness and elastic modulus of precipitate are increased by 10.15 and 32.33 GPa, respectively. The precipitate has higher hardness and lower ductility [9].
Figure 7
Nanoindentation results of the precipitate and metal matrix
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4.2 Wear Results
The wear dimensions on various claw surfaces are shown in Figure 8. On USC (Regions B and D), the wear width on left side is larger than that on right side. The law on LSC (Regions A and C) is the opposite. This situation may be related to the tilt of the movable latch in the running process. Nevertheless, the difference in wear width on various claw surfaces is larger than that on a single claw surface. The USC has higher wear width than LSC. The total wear width reaches the largest value of 20.55 mm in Region D. Figure 8b shows wear scar profiles at the center of movable latch. Materials removal is found on each claw surface. Same as the wear width, the wear depth on USC is larger than that on LSC.
Figure 8
Wear dimensions on various claw surfaces
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To better analyze the wear conditions of movable latch on various claw surfaces, wear area, volume, and depth distribution are shown in Figure 9. In Figure 9a, the wear area on USC is higher than that on LSC. The wear volume of each claw surface varies greatly. The wear volume from Region A to Region D is 12.3, 26.3, 9.6, and 37.4 mm3, respectively. The wear volume in Region D is up to four times higher than that in Region C, which indicates more serious wear occurs on USC. The result of wear depth distribution is counted in Figure 9c for a direct comparison of wear behavior on various claw surfaces. The materials removal between left and right sides is similar for a single claw surface. Material removal on the USC is higher than that on the LSC. As mentioned above, the service behavior on the USC is more complex than that on the LSC, which may be due to the USC suffers extra friction stress [21]. Severe wear will cause a decrease in claw strength [25]. This situation can prove the advantage of double claws because the material removal is shared.
Figure 9
Wear results of movable latch on various claw surfaces
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4.3 Worn Morphologies
Figure 10 shows the OM image in Region E to reveal the corrosion behavior on Co-based alloy surfacing layer. In Figure 10a, the untreated surface covers the track of machining. Pitting pores are found on the surface of movable latch after 6.5 million steps, as shown in Figure 10b. The falling off of carbides may be responsible for this situation [26, 27].
Figure 10
OM image of movable latch in Region E
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Figure 11 shows the worn morphologies on each claw surface. The wear scar on LSC is smooth like a polished surface, as previously reported in Ref. [3]. The wear condition on USC is complex compared to LSC. At the top of claw, the wear scar is still smooth. However, multiple wear debris and grooves are found at the root of claw. This situation indicates that the wear mechanism between USC and LSC is different, ultimately leading to the difference in wear volume.
Figure 11
Worn morphologies on various claw surfaces
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Three typical degradation morphologies of movable latch are shown in Figure 12. The untreated surface has no distinct precipitates, as shown in Figure 12a. The obvious track of machining demonstrates no wear occurs in Region E. Because the boundary of precipitates is preferred for corrosion, the surface in Region E presents the feature of distinctive precipitates with some pitting pores (Figure 12b). Figure 12c shows the typical SEM morphology of LSC. The smooth worn surface indicates the dominant wear mechanism in the low claw is plastic deformation caused by impact wear [28]. Because the hard carbides have low ductility, some cracks can be observed in carbides under the action of cyclic plastic deformation. The typical morphology on USC in Figure 12d presents a severely worn feature. The cracks also exist in the carbides. Besides, grooves and wear debris can be detected on USC, proving abrasive wear occurs on USC.
Figure 12
Degradation morphologies of the movable latch in various regions
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Figure 13 shows the cross-sectional morphologies in various regions. On the side of pinhole, some cracks are observed from the surface to the inner portion along the boundary of carbides. The fall-off of carbides causes the formation of defects on the surface. On LSC and USC, there are some cracks inside carbides rather than the boundary of carbides. The carbides become smaller particles and fall off from the surface under the combined action of impact wear and corrosion. The material removal causes the defect caused by corrosion is not distinct.
Figure 13
Cross-sectional morphologies of movable latch in various regions
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4.4 Analysis of Wear Mechanism
The degradation mechanism of movable latch in various regions is shown in Figure 14. The boundary of carbide is preferred for corrosion because the formation of carbides depletes the Cr element at its boundary [11‐16]. A galvanic couple forms between the carbides (cathode) and its boundary (anode). With the increase in corrosion time, the boundary of carbides is almost corroded away and the deeper carbides will be exposed to high temperature water [20]. As a result, in Region E, the crack initiates at the surface and propagates along the carbide boundary to the inner portion. Besides, corrosion also causes the spalling of carbides, resulting in formation of defects and pitting pores [26]. Corrosion only occurs at the surface layer about a few tens of microns after 6.5 million steps, as shown in Figure 13, which indicates the effect of corrosion is slight at high temperature water. However, the corrosion also promotes wear on USC and LSC.
Figure 14
Degradation mechanism of movable latch in various regions
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Due to the various operating conditions, the degradation mechanism on USC and LSC are not the same. The LSC mainly suffers impact stress, while USC also suffers friction stress [21]. The dominant wear mechanism on USC is plastic deformation caused by impact wear. The wear scar is smooth like a polished surface (Figure 11). Besides, the cyclic impact will cause the fragmentation of carbides. Because the hard carbides have low ductility [3], the high strain caused by plastic deformation leads to cracks inside carbides (Figure 12c). The broken carbides become smaller and easier to fall off from the surface due to the combined action of corrosion and impact wear. Mechanical impact wear continuously destroys the surface and causes effective material removal, which inhibits the expansion of crack and the formation of large pitting pores. Therefore, there is no crack at the boundary of carbides, and the pitting pores are very small.
The top and root of USC have distinct wear morphology. At the top of USC, the wear scar morphology is similar to LSC (Figure 11). This situation proves the wear mechanism of USC contains plastic deformation caused by the impact wear. When the movable brings the drive shaft upward or downward for a specified length, the relative movement occurs at the interface between movable latch and drive shaft. A tangential friction pair forms at the interface as the drive shaft has weight. The exfoliated carbides play the role of abrasive particles [29, 30]. Harder carbides erode the surface, leading to the formation of grooves. Accordingly, the USC also suffers abrasive wear, resulting in more serious wear on USC, as shown in Figures 8, 9, 10, 11, 12, 13.
5 Conclusions
Based on a comparative study of the movable latch in various regions, the degradation mechanism of the movable latch serviced in high temperature water was investigated. Thus, the following conclusions were drawn.
(1)
The formation of carbides depletes the Cr element at its boundary and the galvanic couple forms between the carbides (cathode) and its boundary (anode), leading to the boundary of carbides being preferred for corrosion. The effect of corrosion causes the formation of cracks and pitting pores near the pinhole (Region E).
(2)
Due to the oscillation of drive shaft between the claw surfaces, the dominant degradation in four claw surfaces is plastic deformation caused by impact wear. So the claw surfaces are smooth and look like polished surfaces. Besides, the high strain caused by plastic deformation leads to the fragmentation of carbides.
(3)
Corrosion will cause the broken carbides is easy to fall off from the metal matrix. The generated fine carbides have high hardness, leading to abrasive wear at the interface between the USC and the drive shaft. It is responsible for higher wear volume compared to the LSC.
Acknowledgements
Not applicable.
Competing Interests
The authors declare no competing financial interests.
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