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  • Original Article
  • Open Access

Structure of Micro-nano WC-10Co4Cr Coating and Cavitation Erosion Resistance in NaCl Solution

  • 1,
  • 1,
  • 2Email author,
  • 2 and
  • 2
Chinese Journal of Mechanical Engineering201730:162

https://doi.org/10.1007/s10033-017-0162-9

  • Received: 29 June 2016
  • Accepted: 4 July 2017
  • Published:

Abstract

Cavitation erosion (CE) is the predominant cause for the failure of overflow components in fluid machinery. Advanced coatings have provided an effective solution to cavitation erosion due to the rapid development of surface engineering techniques. However, the influence of coating structures on CE resistance has not been systematically studied. To better understand their relationship, micro-nano and conventional WC-10Co4Cr cermet coatings are deposited by high velocity oxygen fuel spraying(HVOF), and their microstructures are analyzed by OM, SEM and XRD. Meanwhile, characterizations of mechanical and electrochemical properties of the coatings are carried out, as well as the coatings’ resistance to CE in 3.5 wt % NaCl solution, and the cavitation mechanisms are explored. Results show that micro-nano WC-10Co4Cr coating possesses dense microstructure, excellent mechanical and electrochemical properties, with very low porosity of 0.26 ± 0.07% and extraordinary fracture toughness of 5.58 ± 0.51 MPa·m1/2. Moreover, the CE resistance of micro-nano coating is enhanced above 50% than conventional coating at the steady CE period in 3.5 wt % NaCl solution. The superior CE resistance of micro-nano WC-10Co4Cr coating may originate from the unique micro-nano structure and properties, which can effectively obstruct the formation and propagation of CE crack. Thus, a new method is proposed to enhance the CE resistance of WC-10Co4Cr coating by manipulating the microstructure.

Keywords

  • Cavitation erosion resistance
  • Micro-nano structure
  • WC-10Co4Cr coating
  • HVOF

1 Introduction

Cavitation erosion (CE), which is the predominant cause for the failure of overflow components, can be frequently observed in fluid machinery such as ship propellers and rudder blades, the cylinder liners of marine diesel, turbine impellers and various pumps. Corrosive ocean environment will accelerate the cavitation damage of the overflow parts of ships and drilling platforms. CE has become the central technical problems of the fluid equipment, which threatens the safety of the equipment, reduces the efficiency and increases the cost [1, 2]. Therefore, improving the CE resistance of the materials in fluid machinery has significant economic benefits.

The mechanism of cavitation erosion has not yet fully been understood, as it is influenced by multiple parameters, such as hydrodynamics, component design, service environment and material properties. Because CE occurs only on the surface of components, advanced surface engineering techniques have become the most effective approaches to solve CE problems [3, 4]. Several advanced surface engineering techniques, such as thermal spraying, plasma nitriding, chemical vapor deposition, physical vapor deposition, laser cladding, and hardening have been developed to modify the surface properties of component materials. Among them, thermal spraying methods, including arc plasma spraying (APS), detonation gun(D-Gun), and high velocity oxy-fuel spraying(HVOF) have been commercially applied on overflow components of fluid machinery to enhance the cavitation erosion resistance [5].

WC based cermet coatings are well-known for their outstanding wear resistance [6], which has drawn much attention in the research of CE resistant materials. WC–Co coatings, especially those with nanostructures, have already been successfully applied in a wide range of fluid machinery [7]. Compared with the WC–Co coatings, WC-CoCr coatings possess higher strength and better corrosion resistance and are expected to have more excellent CE resistance in corrosive media like ocean environment [8].

WC particle size in WC based coatings significantly affects its microstructure and properties. Armstrongr [9] proposed that mechanical properties and wear resistance of the WC based coatings would generally increase with decreasing WC particle size. The studies of Ghabchi [10] and Ma [11], et al. showed that optimizing WC size and structure can improve the mechanical properties and wear resistance of HVOF sprayed WC based coatings. Scieska [12] and Li [13], et al. suggested that WC based cermet coatings with a high volume fraction of fine WC particles would exhibit high wear performance. Therefore, nanostructure WC based coatings have been extensively studied for the improvement of the microhardness and wear performance [14, 15]. Tillmann, et al. [16], reported sliding and rolling wear behavior of HVOF-sprayed nanostructured WC-12Co coatings. HONG, et al. [17], revealed cavitation erosion behavior and mechanisms of HVOF sprayed nanostructured WC-10Co4Cr coating in NaCl solution. The researches of Zhao [18] and Chen [19], et al. have demonstrated that the hardness and toughness of nanostructured materials can be improved simultaneously. But Dent [20] and Yang [21], et al. also revealed the decrease of fracture toughness of WC based coatings with decreasing the WC size because of decarburization of nano WC followed by the formation of unwanted carbides, such as W2C, complex Co-W–C, and metallic tungsten, which can also lower the mechanical properties of nanostructure WC based coatings. In order to prevent the decarburization of nano WC and reduce the cost of the nano coatings, Skandan [22] and Ji [23], et al. proposed a new kind of micro-nano WC based coating composed of nano and micro WC grain size, which is expected to obtain dense structure and excellent anti-cavitation performance. But, the structures, properties of micro-nano WC–CoCr coating, e.g., hardness, fracture toughness and CE resistance in corrosive environment, have not been fully understood.

The deposition process is another important factor which influences the structures and properties of WC based cermet coatings. Among all the thermal spraying approaches, HVOF has high flame velocity and moderate flame temperature, which can minimize the decarburization of WC to a low level. Therefore, HVOF is an ideal method to deposit micro-nano WC–CoCr cermet coatings [24, 25].

In this work, micro-nano and conventional WC-10Co4Cr coatings (MC and CC) were deposited by HVOF. The microstructure, mechanical properties, electrochemical performance and CE resistance in 3.5 wt % NaCl solution of the coatings were studied, and the cavitation mechanisms of the coatings were explored. The results can provide important reference for the design of WC–CoCr anti-cavitation coatings in ocean environment.

2 Experimental Procedure

2.1 Coating Preparation

Micro-nano and conventional WC-10Co4Cr composite powders (MP and CP), produced by Ganzhou Achteck Tool Technology Co. Ltd, were sprayed on austenitic stainless steel AISI 316, and their characteristics are presented in Table 1. The WC-10Co4Cr coatings were deposited by JP8000 HVOF equipment using kerosene as fuel and oxygen as oxidant gas, and spraying parameters were optimized as shown in Table 2.
Table 1

Characteristics of two WC-10Co4Cr composite powders

Powder No.

Powder type

Manufacturing method

Nano WC size D/nm

Micron WC size D/μm

Powder size D/μm

Nano WC rate/ %

MP

Micro-nano

Agglomeration

70–180

2.5

20–53

30

CP

Conventional

Agglomeration

1.5

10–45

Table 2

Spray parameters of WC-10Co4Cr coatings by HVOF

Coating No.

Powder type

Oxygen flow V/SCFH

Fuel flow V/GPH

Gun length L/inch

Spray distance L/mm

Powder feed rate M/(g·min−1)

MC

MP

1950

6.5

6

370

75

CC

CP

1950

6

6

370

75

Prior to spraying, the substrate surface was cleaned with acetone and grit blasted with 60 mesh corundum. The thickness of the coatings was controlled in 450±20 μm. All the samples were ground and polished to an average surface roughness Ra≤0.02 μm before any characterizations.

2.2 Characterization

The morphology and microstructures of the powders and the coatings were observed with VHX-2000 digital optical microscope(OM), and FEI Quanta 250 scanning electron microscope(SEM). Phase identification for the powders and the coatings was carried out by a D/max-2550 diffraction meter(XRD) using Cu-K α radiation with λ = 0.154 nm.

Microhardness measurements were performed via HVS-1000 microhardness tester at a load of 300 g for 15 s. The porosity was measured with metallographic 200X photos captured by Axiovet 40 MAT metallographic microscope, followed by porosity calculation using IQ materials software. The fracture toughness K c was calculated according to the Wilshaw Eq. (1) [26] (the result was the average value of ten measurements), where P, a and c are the load of Huayin HV5 type Vickers hardness meter (5 kg), half the length of indentation diagonal and half the length of the crack, respectively.
$$K_{c} = 0.079\frac{P}{{a^{{{3 \mathord{\left/ {\vphantom {3 2}} \right. \kern-0pt} 2}}} }}\lg \left( {\frac{4.5a}{c}} \right).$$
(1)

The electrochemical performance of the coatings was measured by CorrTest electrochemical test system which mainly includes CS300 electrochemical workstation, CorrTest control and data analysis software.

2.3 Cavitation Erosion

Cavitation erosion tests were performed on a J93025 ultrasonic cavitation apparatus according to standard GB/T 6383-2009. The cavitation test parameters were set with a frequency of 20 kHz and a amplitude of 40 µm. 3.5 wt % NaCl solution at 25–28 °C was used as the test liquid in a 1000 mL beaker. The tip of the specimen was immersed into the water 3 mm deep. The schematic diagram of the CE test apparatus is shown in Figure 1 and specimen (its dimension is shown in Figure 2) was attached to the free end of the horn.
Figure 1
Figure 1

Schematic diagram of the CE test apparatus

Figure 2
Figure 2

CE test specimen’s dimensions

TG328 electronic balance with a sensitivity of 0.1 mg was used to determine mass losses. The sample was weighed every 60 min and 16 measurements were carried out. The mass loss result was the average value of three specimen test and the volume loss is the mass loss divided by the material density, while cavitation rate (R c ) is every hour volume loss. For comparison, the 316 stainless steel samples were tested under the same test conditions.

3 Results and Discussion

3.1 Structure of WC-10Co4Cr Powders and Coatings

The SEM micrographs of micro-nano powder (MP) and conventional WC-10Co4Cr powder (CP) are presented in Figure 3. It can be seen that both powders are highly spherical, but more pores exist at the surface of CP powder shown in Figures 3(c) and (d), demonstrating that its density is lower than MP powder. High magnification image shows micro WC particles in MP powder are wrapped by the finer nano-particles and the CoCr binding phase, observed in Figure 3(b).
Figure 3
Figure 3

Micrographs of WC-10Co4Cr powders at different magnification

Various structures of the as-sprayed coating surface can be observed from surface morphology of two WC-10Co4Cr coatings (Figure 4) and micro-nano coating demonstrates better melting condition, less porosity and denser microstructure than the conventional one. The reason is that different structured powders can reach to different melting degrees and possess various kinetic energy during the spraying. As the micro-nano coatings consist of micron-sized and nano-sized WC with large specific surface area and high activity, a considerable portion of nano-sized WC was dissolved into melted CoCr alloy. They would fill in un-molten or semi-molten micro WC particles, forming the micro-nano structure, shown in Figure 4(a).
Figure 4
Figure 4

Surface micrographs of WC-10Co4Cr coatings

The cross-sectional microstructures of the micro-nano and conventional WC-10Co4Cr coatings are shown in Figure 5. No obvious porosity can be observed from the low magnification micrographs (Figures 5(a) and (c)) for two HVOF sprayed coatings and the porosity is both less than 0.5% (Table 3). Moreover, the porosity of micro-nano coating is smaller (0.26 ± 0.07%), which is 39.5% lower than that of the conventional one, since the gap between micro WC particles was filled with dissolved nano WC particles and melted CoCr binding phase.
Figure 5
Figure 5

Cross-sectional micrographs of WC-10Co4Cr coatings

Table 3

Porosity, microhardness and fracture toughness of WC-10Co4Cr coatings

Specimen

Porosity

/ %

Microhardness

HV/MPa

Fracture toughness

K c /(MPa·m1/2)

MC

0.26 ± 0.07

1345 ± 136

5.58 ± 0.50

CC

0.43 ± 0.12

1322 ± 181

3.83 ± 0.52

It can be observed that the nano, submicron and micron sized WC particles exist in micro-nano WC-10Co4Cr coating (Figure 5(b)), while in conventional coating only the submicron and micron sized WC particles can be observed (Figure 5(d)). The submicron sized WC particles in the micro-nano and conventional coatings were produced by the breakage of micron WC particle during the power ball mill process.

3.2 Phase Composition of Micro-nano WC-10Co4Cr Powders and Coatings

Figure 6 represents the XRD results of micro-nano WC-10Co4Cr powder and coating. The XRD pattern of micro-nano powder is mainly composed WC, Co, and Co3W3C crystalline phases. Co3W3C originates from insufficient carbon balance in certain area where the combination of Cr and C occurs during the sintering due to their high affinity. Co3W3C phase disappears in the XRD pattern of the coating, meanwhile a small amount of W2C phase is observed. The results demonstrate that carbides are mainly composed of WC and a small amount of W2C, while serious WC decarburization does not occur in the micro-nano WC-10Co4Cr coating deposited by HVOF. The XRD patterns exhibit no differences with the conventional WC-10Co4Cr powder and coating analyzed by Wang in Ref. [27].
Figure 6
Figure 6

XRD patterns of micro-nano WC-10Co4Cr powders and coatings

3.3 Mechanical properties WC-10Co4Cr coatings

Mechanical properties of WC-10Co4Cr coatings sprayed by HVOF including microhardness and fracture toughness are shown in Table 3. Although the microhardness of two coatings is higher than 1300HV0.3 and obvious difference does not exist, the micro-nano coating obtains an extraordinary fracture toughness of ~5.58 MPa·m1/2, which is 45% higher than that of the conventional one. This outstanding property can provide obstacles to the formation and propagation of cracks during cavitation erosion.

3.4 Electrochemical Properties of WC-10Co4Cr Coatings

Figure 7 shows the potentiodynamic polarization curves of two WC-10Co4Cr coatings and 316 steel in 3.5 wt % NaCl solution. It can be observed that the potentiodynamic potentials of the two coatings are below 316 steel, and micro-nano WC-10Co4Cr coating possesses a higher value than the conventional one. That means the micro-nano coating has more superior electrochemical corrosion resistance due to smaller potential difference between the coating and the substrate in comparison with the conventional one.
Figure 7
Figure 7

Tafel plots of WC-10Co4Cr coatings and 316 stainless steel

3.5 Cavitation Erosion Test Results of WC-10Co4Cr Coatings

Figure 8 presents the cumulative volume losses and volume cavitation rates of the two WC-10Co4Cr coatings and the 316 stainless steel in 3.5 wt % NaCl solution. Figure 8(a) indicates that after 16 h CE, the cumulative volume losses of the micro-nano coating (MC), conventional coating(CC) and 316 stainless steel were 2.31, 3.58 and 15.7 mm3, respectively, in which the cumulative volume losses of MC and CC decreased respectively 85% and 77% compared with 316 stainless steel. Meanwhile, the average volume cavitation rates of the micro-nano coating, conventional coating and 316 steel were respectively 0.122, 0.244 and 0.972 mm3/h. The cavitation rate of MC is only 50% and 12.5% as much as those of CC and 316 steel at the steady CE period (last 5 h). From the result it can be concluded that the micro-nano WC-10Co4Cr coating possesses more excellent CE resistance.
Figure 8
Figure 8

Cumulative volume loss and cavitation rate of WC-10Co4Cr coatings and 316 stainless steel in 3.5 wt % NaCl solution

3.6 Cavitation Mechanisms Analysis of WC-10Co4Cr Coatings

The surface morphologies of the two WC-10Co4Cr coatings with different CE time at the initial period of the tests (≤1 h) are displayed in Table 4. The dark parts in the images are the areas of the eroded coatings by CE. A small amount of pores and scratches were observed on the surface of the coatings before the test due to imperfect polishing. After 0.25 h CE test, CE appeared in the two kinds of coatings with different degree. MC coating has smaller CE areas than CC coating. After 0.5 h CE test, the CE areas of the coatings expanded at different speed and the expanding speed of MC coating was slower than that of CC coating. After 1 h CE test, the eroded area was still small on the surface of MC coating, while around 50% of CC coating area was eroded. These results are in consistence with the curves of cavitation volume loss.
Table 4

Surface micrographs of WC-10Co4Cr coatings at first period of cavitation erosion

CE was produced under the alternating stress caused by bubble generation and collapsed during ultrasonication. At the initial stage, stress concentrated at the pores and defects of the coating would accelerate the plastic deformation of the material in the vicinity. Due to the different crystal structure between WC hard phase and CoCr binding phase, deformation was not coordinated at the interface, which generated the local high stress field, and dislocation stress was accumulated at the grain boundary [27, 28]. When the cumulative stress reached the threshold, intergranular microcracks would generate and subsequently extended under repeated cycle of alternating stress, resulting in the formation of cavitation source. The cavitation source further developed along some preferable angles inside the coating [29, 30]. The formation rate of the cavitation source of the CC coating was higher at the initial stage in 3.5 wt % NaCl solution due to its higher porosity, lower fracture toughness, and electrochemical performance. Under the stress caused by bubble collapse and the repeated impacts of micro jet along with the Cl penetration in the solution, the further extension of cavitation cracks directly lead to the interlamination detachment and WC particles exfoliation, causing the formation of the large-scale CE. On the other hand, the low porosity of MC coating significantly reduced the amount of CE sources and its high hardness and toughness can effectively obstruct the extension of the CE cracks, which enables micro-nano WC-10Co4Cr coating to possess excellent CE resistance in 3.5 wt % NaCl solution.

Figure 9 shows the SEM surface images of two coatings after 16 h cavitation erosion in 3.5 wt % NaCl solution. CE craters with different shapes can be observed on the surface of the coatings. The surface of MC coating is just a little rough (Figure 9(a)), while CE pits with diameter more than 30 μm can be observed clearly on the surface of CC coating as shown in Figures 9(b) and (c).
Figure 9
Figure 9

Crater micrographs of WC-10Co4Cr coatings after 16 h cavitation erosion in 3.5 wt % NaCl solution. (a) MC, (b) CC, (c) CC

4 Conclusions

  1. (1)

    In micro-nano WC-10Co4Cr coating deposited by HVOF, carbides are mainly composed of WC and with a small amount of W2C, no obvious WC decarburization can be detected.

     
  2. (2)

    Micro-nano WC-10Co4Cr coating exhibits better mechanical properties and its fracture toughness is 45% higher than conventional coating. Moreover, the micro-nano WC-10Co4Cr coating demonstrates higher corrosion potential and possesses better corrosion resistance.

     
  3. (3)

    Micro-nano WC-10Co4Cr coating possesses better CE resistance and its CE resistance is enhanced above 50% than conventional coating at steady CE period in 3.5wt % NaCl solution.

     
  4. (4)

    Superior CE resistance of HVOF sprayed micro-nano WC-10Co4Cr coating originates from its high hardness, high fracture toughness, low porosity and excellent corrosion resistance, which can effectively obstruct the formation and propagation of CE cracks.

     

Declarations

Acknowledgements

Supported by National Natural Science Foundation of China (Grand No. 51422507).

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

(1)
State Key Laboratory of Advanced Technology for Materials and Processing, Wuhan University of Technology, Wuhan, 430070, China
(2)
School of Energy and Power Engineering, Wuhan University of Technology, Wuhan, 430063, China

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© The Author(s) 2017

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