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Advances in Materials Science and Engineering

Volume 2013 (2013), Article ID 615464, 7 pages

http://dx.doi.org/10.1155/2013/615464

## Optimization of Ni-Based WC/Co/Cr Composite Coatings Produced by Multilayer Laser Cladding

Department of Mechanics, Mathematics and Management, Polytechnic University of Bari, Viale Japigia 182, 70126 Bari, Italy

Received 7 January 2013; Accepted 29 April 2013

Academic Editor: Roham Rafiee

Copyright © 2013 Andrea Angelastro et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

#### Abstract

As a surface coating technique, laser cladding (LC) has been developed for improving wear, corrosion, and fatigue properties of mechanical components. The main advantage of this process is the capability of introducing hard particles such as SiC, TiC, and WC as reinforcements in the metallic matrix such as Ni-based alloy, Co-based alloy, and Fe-based alloy to form ceramic-metal composite coatings, which have very high hardness and good wear resistance. In this paper, Ni-based alloy (Colmonoy 227-F) and Tungsten Carbides/Cobalt/Chromium (WC/Co/Cr) composite coatings were fabricated by the multilayer laser cladding technique (MLC). An optimization procedure was implemented to obtain the combination of process parameters that minimizes the porosity and produces good adhesion to a stainless steel substrate. The optimization procedure was worked out with a mathematical model that was supported by an experimental analysis, which studied the shape of the clad track generated by melting coaxially fed powders with a laser. Microstructural and microhardness analysis completed the set of test performed on the coatings.

#### 1. Introduction

Increasing attention is given to metal matrix composites (MMC) consisting of hard and brittle carbide particles embedded in a tough metal binder. Carbide-metal matrix composite materials are characterized by a high resistance to all types of wear. It is due to a positive combination of properties given by hard phase particles included in a tough matrix, capable of reducing stresses by plastic deformation. The superior wear resistance of Tungsten Carbide and in particular of WC/W_{2}C or WC-Co as hardfacing material is well known, while Co- or Ni-based alloys are mostly used as binders.

Laser cladding is capable of producing a wide range of surface alloys and composites of required properties [1]. In the last years, LC has shown a growing interest due to its capability of introducing hard particles such as SiC, TiC, and WC as reinforcements in the metallic matrix such as Ni-based alloy, Co-based alloy, and Fe-based alloy to form the ceramic-metal composite coatings, which have very high hardness and good wear resistance [2–7].

Nickel-based alloys have a unique combination of properties that enables them to be applicable in a variety of applications. Specifically, Nickel-based alloys coatings, with high bonding strength, a better corrosion behavior, and excellent resistance to adhesive and abrasive wear, have promising applications in engineering [8].

Laser cladding with metal-WC composite coating has shown high potentiality for enhancing wear resistance since WC combines high hardness, low coefficient of thermal expansion, good plasticity, and wettability by molten metals.

Several works can be found in the literature on the laser cladding processing of Nickel-based and WC composite coatings.

Chen et al. [9] presented an investigation on laser cladding of a composite alloy powder consisting of 35% WC particles and Ni-Cr-B-Si alloy on mild steel substrate, producing a high resistance composite coating with a strong metallurgical bond and minimal dilution.

Wu et al. [10] demonstrated that high-quality Nickel-based and 60% WC composite coatings can be produced controlling laser cladding processing parameters.

Van Acker et al. [11] explored laser cladding of Ni-WC/W_{2}C MMC coatings on low carbon steel substrates, using a CO_{2} laser. They made different coatings with three different particle sizes of the carbides and volume fractions ranging from 0% up to 50%. A clear dependency of the wear resistance on the carbide concentration was found, which was more pronounced for the coatings with the finest WC/W_{2}C carbides. They found that a small amount of carbides is sufficient to improve the wear resistance drastically.

Zhou et al. [12–14] investigated the relationships between some processing parameters (i.e., laser specific energy, powder density, preheated temperature of substrate, and types of substrate) and the structure characteristics of Ni-based WC composite coatings during laser induction hybrid rapid cladding (LIHRC), finding that crack-free composite coatings with smooth surface and good profile can be prepared by LIHRC on the different substrates.

In LC, laser beam is focused and moved on the top surface of the substrate producing a molten pool where a metal powder flow is injected. Powder totally melts and then quickly resolidifies creating a track, characterized by high density and by good bonding to the substrate. The first layer is realized depositing tracks one next to the other, with a designated amount of overlap (Figure 1). After the deposition of the first layer, in multilayer laser cladding (MLC), the laser head, which includes focusing lens and powder delivery nozzle, is raised in the positive -direction and starts deposition of the second layer. Therefore, process recurs, line-by-line and layer-by-layer, until the entire component is built up.

In the present investigation, the Ni-based WC/Co/Cr composite coatings made by the multilayer laser cladding technique were studied. An optimization procedure, which used a mathematical model, was applied. The mathematical model, based on previous research studies [15–18] allowed calculating the optimal values of the laser translation speed and of the hatch spacing between adjacent vectors and between layers of the deposited material. The presented methodology allowed selecting the optimal combination of parameters that produced low porosity, crack-free, and good bond between the layers of the coatings.

#### 2. Materials and Methods

##### 2.1. Experimental Setup and Materials

A mixture of 30% Colmonoy 227-F and 70% WC/Co/Cr powders was used as the coating material. The composition of both powders is listed in Table 1. Colmonoy 227-F is a commercially available product of Wall Colmonoy consisting of Ni alloy with maximum particle diameter of 106 *μ*m. This material, characterized by an elevated hardness (22–27 Rockwell C), a density of 8.53 g/cm^{3}, and a melting point of 915°C, is able to tolerate extreme job conditions because of its elevated resistance to abrasion, corrosion, stresses, and high temperatures [19–21].

The other material is Sintered T311, commercially produced by MBN Nanomaterialia S. p. A. (maximum particle diameter 49 *μ*m). This powder is characterized by an elevated amount of WC (about 86% wt) and by the presence of Co (10% wt) and Cr (4% wt).

The substrate material consisted in AISI 304 steel.

The equipment used for cladding was a 3 kW CW CO_{2} laser system, together with a powder supply system consisting of a pneumatic conveyor, a splitter, used to mix and divide the flow into three equal flows of carrier gas and powder mixture, and, finally, a coaxial nozzle having the function to direct the three powder flows coming from the splitter in the weld pool.

In order to optimize the process parameters, a mathematical model based on previous research studies [15–18] was implemented. In detail, the model allowed calculating optimal values of translation speed of the laser beam (TS) and of hatch spacing between adjacent vectors () and between layers () of the deposited material (Figure 2). The other process parameters were kept constant.

The laser beam was set to 2.4 kW and laser spot diameter to 2 mm. Argon was used as shielding gas with a flow rate of 12 L/min and helium was used as carrier gas with a flow rate of 5 L/min. The powder mixture of the two kinds of materials was created in the splitter. The total powder feed rate PFR_{tot} of the powder mixture was 9.3 g/min.

##### 2.2. Optimization Model

The mathematical model used in this work is based on the following hypotheses [15–18].(1)The deposition process is stationary: the quantity of powder at each deposited track is identical; the cross-section area of each track is uniform. (2)The cross-section of the deposited track is geometrically similar, with some degree of approximation, to an arc of circumference of height and width (Figure 2). The area of this section is also calculated as a function of the only variable , once fixed a certain value of the ratio between and (). This approximation is justified, neglecting gravitational forces and the variation of the density of the melt zone with the temperature and with the concentration of alloy components. In fact, if the surface tension remains constant, the balance of forces that occurs at the interface molten zone/air ensures that its profile has radius constant .(3)The width and the deposition efficiency (defined as the ratio between the amount of deposited material and used powder) are linearly dependent on the translation speed TS.

Therefore, knowing the value of the density () of the material to be deposited and the set of the other process parameters, including PFR_{tot}, , and , it is possible to calculate the value of TS, to guarantee, with a small margin of error, the desired size of the cross-section of the single track.

Moreover, knowing values of and , it is possible to calculate the value of the hatch spacing between adjacent tracks (), along the -direction, which ensures a certain geometric regularity of the final surface of each deposited layer. Additionally, it is possible to calculate an optimal value of the hatch spacing between adjacent layers of material (), along the -direction. This value has to guarantee a degree of overlap (*O*_{%}) which maximizes the relative density of deposited tracks and that produces a good adhesion between different layers.

In detail, according to the above hypothesis 1, it is possible to introduce the following equation: where , , and are the areas of specific regions, as illustrated in Figure 3.

In addition, it is possible to calculate the cross-sectional area (mm^{2}) with the following relation:

Finally, it is possible to obtain optimal values of (mm) and of *O*_{%} with the following relations:

According to Zhang et al. [16], the best results can be obtained for values of lower than a critical value , as shown in the following:

##### 2.3. Calculation of the Model Coefficients

The hypothesis of linear dependence of the width on the translation speed TS can be demonstrated by means of (6) [16]:

Single-track clads were realized by LC on three AISI 304 plane substrates (Figure 4) in order to estimate the coefficients and .

Three values ****of the translation speed TS were chosen (500–750–1000 mm/min) to perform the three single-track clads shown in Figure 4. Then, the single-track widths were measured. Their values, shown in Table 2, allowed to calculate and :

The same process parameters were used to create other three samples, obtained by depositing six clads of the composite material on the AISI 304 substrate. The purpose was to obtain the coefficients (, ) of (8), which shows the linear dependence of the deposition efficiency on the translation speed TS:

The masses of the deposited material and of the feed powder were derived, for each sample, from (9) and (10), respectively: where (g) is the total mass measured by weighing the sample after the laser deposition, (g) is the plate weight measured before the laser deposition, and (mm) is the total length of the six clads. Hence, it was possible to calculate the average deposition efficiency as follows:

The results in Table 3 allowed calculating both and using

##### 2.4. Calculation of the Optimal Translation Speed

The density of the powder mixture () was calculated by (13) as the sum between the weighted average densities of the two powders, adopted as their weights wt% within the mixture:

A value of 12.2 g/cm^{3} was found for .

Equation (14) [15] shows the relationship between the powder feed rate PFR_{tot} (g/min), the density , the clad cross-section area , and the deposition efficiency * η*:

The clad cross-section area (mm^{2}), defined by (2), can be expressed as a function of and , as indicated in the following:

The was set at the value 1/3, as indicated in the following:

Finally, after setting values of PFR_{tot} (9.3 g/min) and of (12.2 g/cm^{3}) and solving the system of (7), (12), (14), (15), and (16), the optimal TS value was discovered (mm/min).

Later on, in order to check the mathematical model validity, a single clad was produced setting kW, PFR_{tot} = 9.3 g/min, and TS = 170 mm/min. The real height and the width of the single clad were measured, and the experimental value was found. This value was compared with the theoretical value = 1/3 (16), and the percentage error , defined by (17), was calculated and found to be equal to 9.9%. Results are shown in Table 4:

Since the percentage error was maintained below 10%, the mathematical model was considered reliable. This result is in line with the one found by Angelastro et al. [17] that used the same methodology to determine optimal deposition parameters for Colmonoy 227-F, determining a percentage error of 7.4%.

##### 2.5. Multilayer Composite Sample Fabrication

A multilayer sample, consisting in the LC deposition of four layers of the composite powders on AISI 304 steel substrate, was prepared. Every layer consisted of tracks all parallel to each other; in detail the first and the third layers (odd layers) were produced by four tracks and the second and the fourth layers (even layers) by three tracks.

The optimal process parameters, derived from the previous mathematical analysis, were used for the fabrication of the sample. The optimal geometrical parameters, consisting in determining values of hatch spacing (mm) and (mm), defined in Figure 3, were calculated by (18) ( is the circumference radius). Process and geometrical parameters used in the fabrication of the multilayer composite sample are summarized in Table 5.

#### 3. Analysis of Results

The implementation on an analytical model allowed determining the optimal translation speed and hatch distances between adjacent vectors () and between layers () to obtain well-shaped multilayer composite deposits on a stainless steel substrate.

The multilayer sample was cut, polished, and etched for macro- and microstructure examinations along the transverse cross-section. An optical microscope was used to analyse the macro- and microstructure of the sample.

The macrostructure of the transverse cross-section is presented in Figure 5. The macrostructure of the cross-section reveals a pattern of layer-by-layer deposition. Moreover the deposited material appears free of cracks and with a limited number of pores. Specifically, the analysis of porosity was performed using an image processing software. A maximum porosity of 0.24% was found with an average pore diameter of 0.29 mm.

The interface with the AISI 304 substrate was wavy and showed metallurgical bonding (Figure 6(a)).

Figure 6(b) shows the image of the 30% Colmonoy-70% T311 laser cladding. It can be seen that there is a matrix of Cobalt and Nickel that separates the carbide particles. The sharp edges of the WC are clearly visible. The distribution of WC particles in the matrix is uniform.

The average microhardness of the deposited composite material was measured at various locations along the transversal section of the sample using a Vickers indenter Remet HX1000 applying a 300 gf load for 15 s. Figure 7 shows the microhardness profile along the cross-section of the deposited layers on the base metal. It can be seen that the average microhardness of the bulk composite coating (approximately 700–720 HV) is about 3.5 times as much high as that of the stainless steel substrate (approximately 206 HV). The increase of the hardness can be attributed to the formation of WC hard phases, which are homogeneously dispersed in the matrix.

#### 4. Conclusion

Ni-based alloy (Colmonoy 227-F) and Tungsten Carbides/Cobalt/Chromium (WC/Co/Cr) composite coatings were fabricated by MLC on AISI 304 steel substrate. A mathematical model was used to calculate optimal values of the laser beam translation speed (TS) and of the hatch spacing between adjacent vectors () and between layers of the deposited material ().

A uniform distribution of WC particles was observed in the matrix of Cobalt and Nickel, which allowed reaching a microhardness of approximately 700–720 HV in the composite laid down material. The increase in the hardness profile was attributed to the formation of a hard phase during the laser cladding process.

The deposited layer had a maximum porosity of 0.24%. The composite coating was crack-free and characterized by good adhesion with the substrate and between layers.

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