Effect of Plasma Cladding Speed on the Microstructure and Properties of ZrC-ZrB₂/NiAl Coating

Abstract

NiAl composite coating strengthened by ZrC and ZrB₂ phases is synthesized by the plasma cladding process. The influence of cladding speed on microstructrue and properties of coatings is studied. The main phases of coatings are NiAl, γ-(Fe,Ni), ZrC and ZrB₂ phases. ZrC is in the shape of points and small blocks, ZrB₂ shows long strips and needle bar. The slower the cladding speed, the larger the size of the reinforcing phases. With the increase of cladding speed, the wear resistance of the coatings improves. Coating with the cladding speed of 10mm/s has excellent wear-resistance property owing to high hardness and low friction coefficient. ZrC and ZrB₂ strengthening phases play an important role. The main wear mechanism of NiAl composite coating is adhesive wear.

Keywords:
ZrC-ZrB₂/NiAl composite coating; in-situ synthesis; wear resistance; microhardness

1. Introduction

Wear caused by mechanical friction is the interaction between parts and other components. The wear failure makes great economic loss¹. Indirect losses caused by fracture and abrasion are more difficult to statistics. It is necessary to explore wear resistant of coating to improve the surface properties of metal materials.

Metal-matrix composite (MMC) coatings have excellent properties, such as specific stiffness, good thermal conductivity and good corrosion resistance, high modulus, stability at high temperature and wear resistance^2-4. They are comprehensive applied as promising candidates of advanced materials.

The NiAl intermetallic compound which has low density, high melting point, good corrosion resistance, good oxidation resistance and heat conduction performance is widely used as high temperature structure material and coating material^5-7. However, the low strength and plasticity at high temperature confine its application^8-10.

The ceramic phase has the advantages of high strength and high hardness. ZrC and ZrB₂ phases have a series of advantages such as high melting point and hardness, high temperature stability, strong wear resistance^11,12. There are many literatures about the composites or coatings which are strengthened by ZrC or ZrB₂ phases^13-17. Those materials have good properties such as wear resistance^13,16, ablation resistance¹⁵, oxidation resistance¹⁷, and so on. It is anticipated that the ZrC-ZrB₂/NiAl composite coating with excellent corrosion resistance and wear resistance can act as a candidate coating materials in many fields.

Plasma cladding process is widely used to many industrial aspects because of high heating, good controllability and low cost^4,18,19. At present, there are relatively few studies on the effect of scanning speed on the properties and microstructure of coatings by plasma cladding. In this work, the ZrC-ZrB₂/NiAl coating is fabricated by plasma cladding process. The influence of plasma cladding speed on the properties and microstructure is investigated. It is of great significance to optimize the technological parameters of plasma cladding and improve the properties of coating.

2. Experimental Procedures

The raw materials are commercially available Ni powder(purity 99.5%), Al powder(purity 99%), B₄C(purity 97%) and Zr(purity 99%), which are used to prepared the NiAl composite coatings. The matrix of composite coating is Ni and Al with the atomic ratio of 1:1. The ZrC and ZrB₂ phases are created by the reactions of 3Zr+B₄C→ZrC+2ZrB₂. The mass percent of ZrC-ZrB₂ strengthening phases is 30% in the coating. Alloy powders are mixed uniformly in a three-dimension blender for six hours. The total mass of coating powders is 10 grams. The mass of Ni, Al, Zr and B₄C is differently about 4.8 grams, 2.2 grams, 2.5 grams and 0.5 grams. The average size of mixed powders is about 75-110μm. Substrate material used in this experimental is Q235 low carbon steel which has the size of 120mmx50mmx5mm. The nominal chemical composition is (wt. %): C 0.15, Mn 0.45, Si 0.3, bal. Fe. The mixed homogenous powder is pressed on the surface of Q235 with sodium silicate solution (as binder) and the thickness of pre-coating is about 1 mm with the scan cladding speeds of 8mm/s (coating 1), 9mm/s (coating 2), 10mm/s (coating 3), respectively. The NiAl composite coatings are produced by plasma cladding process. The process parameters of plasma cladding are listed in Table 1. The metallo-graphic sample is cut along the cross-section of the coated samples. The microstructure is observed by Nikon ME600 optical microscope. The composition is analyzed by JXA-8230 electron probe microanalysis (EPMA). The phase of the prepared composite coating is identified by X-ray diffraction (XRD) with Cu Kα radiation. Vickers microhardness testing is carried out with a load of 50 g in 15 seconds on FM-700/SVDM4R Automatic micohardness tester. The tribological tests of the coats are performed by using CETR-UMT-3MO multifunctional friction and wear testing machine with a GCr15 friction wheel (hardness HRC63) and a load of 50 N under dry sliding conditions. The wear volume of the coating is measured by a 3D topography instrument.

Table 1
Parameters of plasma cladding.

Current(A)	90
Voltage(V)	30
Scanning velocity (mm/min)	600
Plasma gas flow (Ar,m3/h)	0.2
Protective gas flow (Ar,m3/h)	0.5

3. Results and Discussion

3.1 Microstructure of coatings

Figure 1 shows the EPMA micrographs of Ni, Al, Zr and B₄C raw powders. The Ni and Al powders present spherical shapes and the size is the range of 45-75μm. The Zr and B₄C powders present cuttings shape and granular, the size is about 20-75μm. All of the powders are mixed uniformly and make sure the good flowability and full reaction.

Figure 1
EPMA micrographs of raw powders of (a)Ni (b)Al (c) Zr (d)B₄C.

Figure 2 demonstrates the XRD patterns of coatings obtained by different cladding speed. The original powders are not detected in XRD,which indicates that the reaction has been fully carried out as expected. It can be seen from Figure 2 that microstructure of NiAl composite coatings is mainly composed of NiAl, γ-(Fe, Ni), ZrB₂ and ZrC phases. The surface of Q235 and raw powders are melted and a molten pool is formed during the plasma cladding process. The diffusion of elements such as Fe, Ni and Al atoms will generate at the interface of the substrate and the coating. Fe atoms diffuse from the substrate to the coating and solute into Ni atoms. They form γ-(Fe, Ni) solid solution. The diffusion is discussed later at the end of section 3.1.

Figure 2
XRD patterns of the NiAl composite coatings.

Figure 3 shows that cross-sectional micrograph of coating 2. The coating is compact and uniform. The transition zone from coating to substrate is continuous. The interface between coating and substrate is free obvious porosities and cracks. It indicates that the coating has good formability and forms metallurgical bonding with the Q235 steel.

Figure 3
Cross-sectional micrograph of coating 2.

It can be seen the shape and size of strengthening phase in Figure 4. The size of long bar reinforcement is about 3-5μm when the cladding speed is small (Figure 4a). The bar strengthening phase becomes fine with the rise of cladding speed (Figure 4b, c). The size of bar reinforcing phase is about 1-2μm when the cladding speed is 100mm/s (Figure 4c). There are two different shape phases. The one has the shape of needle or long bar and the other one is petals and small block shape. The main elements of long bar or needle phase is Zr and B in Figure 4e according to B point in Figure 4c. It is ZrB₂ phase. The energy spectrum analysis of small block or petals phase is shown in Figure 4f according to the C point in Figure 4c, which contains Zr and C elements. It is ZrC phase. The main elements of the matrix are Ni, Al and Fe (Figure 4d according to the A point in Figure 4c). The main phases of coating matrix are NiAl and γ-(Fe,Ni). During plasma cadding Fe diffusses from Q235 steel to coatings resulting in the formation (Fe, Ni) phase¹⁸.

Figure 4
EPMA microstructure of the composite coatings (a) coating 1 (b) coating 2 (c) coating 3 (d) EDS of coating matrix (e) EDS of ZrB₂ (f) EDS of ZrC.

The width of ZrB₂ gradually reduces with the raising cladding speed (Figure 4ac). The coating and substrate are melted and form molten pool by the plasma heating. The volume of melted pool is large for gaining more energy when the cladding speed is small. The solidification time is prolonged. The strengthening phase has more time to grow. So the size of ZrB₂ in the coating 1 is larger than that in coating 2 and coating 3 (Figure 4).

Surface scan map of coating 1 is shown in Figure 5, which can further illustrate the corresponding relationship between the strengthening phase and the element distribution. Figure 5a shows the microstructure of coating 1. It demonstrates the needle bar shape and small block grains clearly. Figure 5b shows that C element is mainly distributed in block or petals phase. Figure 5c and d show the distribution of B and Zr elements respectively. These elements are mainly distributed in the bright grey needle bar-like area. It can be deduced that the bright grey particles with needle or long bar shapes are ZrB₂ and the small block particles around the needle bar are ZrC. Figure 5e and f show that Ni and Al elements. They are mainly distributed in the area outside the needle bar. Two elements are always distributed in the same area. The main phases outside the needle or bar phase region are NiAl.

Figure 5
Surface scan map of coating 1 ( color and brightness represent the intensity of corresponding element).

The reaction between raw powders is induced by the massive heat released by plasma cladding process. The Al and Ni powders first melt for low melting points. NiAl phase is fabricated by the reaction of Al and Ni. Then Zr powder starts to melt for lower melting point (1852°C) than that of B₄C (2350°C) by plasma cladding process. Liquid Zr clads B₄C. The molten Zr reactes and forms ZrB₂ and ZrC with B₄C through a liquid-solid diffusion. The B₄C is decomposed into 4[B] and [C] in high temperature molten pool by plasma heating further. There exist more [B] than [C] in molten pool. The liquid phase will be beneficial to the reaction of Zr and B₄C. The ZrC is first nucleated for higher melting point (3540°C) than that of ZrB₂ (3250°C). Subsequent, ZrB₂ nucleates. ZrB₂ has hexagonal structure. The favorable growth direction is [0001]. The growth speed of [0001] direction is rapid. The ZrB₂ has the morphology of needle or stick shape. ZrC has face centered cubic structure. The growth speeds of every direction is near equal. ZrC has the block shape.

Figure 6 shows the element line scan of the coating 3. A, B and C points represent the surface of the coating, the interface and the substrate respectively. It shows that Fe element gradually reduces from substrate to the coating. Al and Ni elements gradually increase from substrate to the coating. There are no abrupt element fluctuations, which indicates that the coating has formed a good metallurgical combination with the substrate.

Figure 6
Line scanning of coating 3 (a) coating 3 and (b)(c)(d) element distribution

3.2 Coating properties

The microhardness curves of coatings from surface to substrate are shown in Figure 7. The hardness of the coating gradually increases with the rising distance from coatings surface and it reaches the highest ( about HV780 of coating 3). Then it starts to decrease and finally the hardness is stable in the substrate (about HV180). The hardness of the coatings surface is not the highest. The pre-coating and partial substrate are melted and form molten pool by plasma arc heating. The metal begins to solidify when the plasma arc leaves. The coating near substrate first crystals by substrate chilling. The coating surface finally solidified. There are a small amount of porosities and defects on the coating surface. Due to the high temperature of plasma arc, the elements of Ni, Al and Zr on the surface of coatings seriously are burned loss. In addition, the bottom of coating has large cooling rate and high temperature gradient because the heat is absorbed by substrate. The temperature of the substrate rises rapidly due to absorption of heat. The cooling rate of the molten pool reduces and the temperature gradient lows when the surface alloy of coating solidifies. There is large supercooling area. The strengthening phases have enough time to nucleate and grow. The size of the reinforcing phases are relatively larger in the surface of coating. The smaller size of the strengthening phases, the better strengthening effect on the coating. All of these reasons cause lower hardness on the surface of coating.

Figure 7
Microhardness curves of NiAl composite coatings.

The hardness is the highest at 250-450μm from the surface of the coating. The density of B element and C element are low, which are easy to gather at the surface of the molten pool. There is more reinforcing phases than that in bottom. Therefore, the hardness of the coating is higher than the bottom of the coating.

The hardness curve of the coating is not consistent by different cladding speed. It is related with the size of strengthening phases and surface formability. The hardness of coating 3 is the highest. The mean hardness of coating 3 (about 700 HV) is more than three times that of the substrate (about 180HV). The coating 3 contains a large amount of ZrC and ZrB₂ reinforcing phases. When the coatings are subjected to external pressure, the strengthening phases increase the resistance to dislocation movement. The hardness and strength of reinforcing phases are much higher than that of the Q235 substrate. The cladding speed of coating 3 is 10mm/s. The temperature of molten pool is lower than that of coating 1 and coating 2 with the cladding speed of 8mm/s and 9mm/s. The element burn in the coating 3 is slight. The size of reinforcing phases of coating 3 is small (Figure 4). The fine ZrC and ZrB₂ phases have better strengthening effect on the coating 3. The hardness of coating 3 is higher.

Figure 8 shows the friction coefficient of coatings and Q235 steel in the course of tribological test. In the initial stage, the friction coefficient of coatings and Q235 substrate has a large change. Then the stable stage arises. The stable stage of Q235 steel occurs after 1400s during tribological test. The friction coefficient is about 0.66. The friction coefficient of coating 1 is between 0.55 and 0.64. The friction coefficient of coating 2 has the larger fluctuation as time goes. The friction coefficient is between 0.48 and 0.55, which may be resulted from surface properties and other defects. The friction coefficient of coating 3 is between 0.42 and 0.45, which is the minimum. The friction coefficients of coatings are lower than that of Q235. The strengthening phases are uniformly dispersed in the coatings, which has better strength to coatings. The indenter is difficult to penetrate deep into the coatings and can only reciprocate slightly on the surface of the coatings. The friction coefficient of coating is low. The oxide films are formed both on the NiAl matrix and reinforcing phases during tribological test²⁰. They further act as protective layer. This is another reason that the friction coefficient of coating is lower than that of Q235 steel. The size of strengthening phases is the smallest (Figure 4c), which makes coating 3 has the highest hardness. The friction coefficient of the coating 3 is the lowest.

Figure 8
Variation curves of friction coefficient of coatings with the time.

The wear volume of Q235 steel and coatings is shown in Figure 9 after tribological test for 3600s. It indicates that Q235 substrate has the largest wear volume 25.14×109μm³. The wear volume of coating 3, coating 2 and coating 1 is 4.96×10⁹μm³, 9.73×10⁹μm³ and 10.07×10⁹μm³ respectively. The wear volume of coating 3 is the minimum. The experimental results show that the wear resistance of the coatings is superior to that of the substrate for the existence of strengthening phases.

Figure 9
Wear volume of coatings.

The worn morphology of coatings and Q235 substrate are showed in Figure 10. Q235 has the characteristics of low hardness and good plasticity. The hardness of GCr15 steel ball as the friction pair is 63HRC, which is far harder than the Q235. Hence the steel ball is easy to penetrate into the surface of the Q235 for reciprocating cutting. When the prominent points of GCr15 ball have sharp edges and appropriate angle, it creates long and deep grooves (indicated by arrow in Figure 10b ). It is severe abrasive wear. When the prominent points of GCr15 ball have smooth edges. It can push some metal on the surface of the Q235 to the sides of the furrow and form a microscopic plough (Figure 10b). Since the abrasion process is repeated, the plow wrinkle will harden and fall off. It forms the worn debris. The worn debris detaches from the surface of Q235. Therefore, the adhesive wear is also a wear mechanism of Q235 substrate.

Figure 10
The worn morphology of Q235 and composite coatings (a)(b) Q235 substrate (c)(d) coating 1 (e)(f) coating 2 (g)(h) coating 3.

The worn morphology of coatings are different from that of Q235. The coatings hardness are far higher than that of Q235 substrate. The GCr5 ball can hardly penetrateinto the surface of the coatings. There are a few furrow and scratches (Figure 10d, f, h).

The size, volume fraction, distribution of the ZrC and ZrB₂ particles have a great effect on the wear resistance of NiAl-based composite material. The reinforcing phases of high hardness can prevent the abrasive particles from being pressed into the surface of NiAl composite coatings during friction test. ZrC and ZrB₂ reinforcements can take main load during sliding. Therefore, the worn surfaces are smooth and the grooves are narrow (Figure 10c, e, g). The main wear mechanism of NiAl-based coating with ZrB₂ and ZrC reinforcing particles is adhesive. The reinforcement size of coating 3 is about 1-2μm, which is smaller than that of coating 1. Coating 3 has high hardness. Coating 3 has higher wear resistance as compared with coatings 1 and 2. There is slight scratch on the worn surface of coating 3 (Figure 10h).

The oxide film can improve the wear resistance of composite coating. The Ni, Al and Fe elements are oxidized and oxide films are formed on the surface of matrix during the tribological test. The oxide films of ZrC and ZrB₂ grains can also been formed on the surface of reinforcements. The oxide films act as a protective layer which prevents the adhesive interaction of mating surfaces²⁰. It makes the composite coatings good wear resistance. The worn surface of composite coatings is smooth and has few and shallow furrows(Figure 10c, e, g).

4. Conclusions

1. 1

   ZrC-ZrB_2/NiAl composites coatings are prepared by plasma cladding technology with Zr, B₄C, Ni and Al powders as raw materials. There are not any cracks and porosities in the coatings. The coatings have good metallurgical bonding with substrate.

2. 2

   The microstructure of composite coatings is consist of NiAl, γ-(Fe,Ni),ZrB₂ and ZrC phases. ZrB₂ shows long needle bar shapes and ZrC shows small block shape. As the cladding speed increases, the size of the ZrB₂ phase gradually becomes finer.

3. 3

   The hardness and wear resistance of the coatings are much higher than the Q235 substrate. Coating 3 has the excellent properties because the strengthening phases are the finest and the surface is less burnt.

4. 4

   The wear mechanism of Q235 is severe abrasive wear and severe adhesive wear. The wear mechanism of the NiAl-based coatings mainly is adhesive wear.

5. Acknowledgments

This research was supported by National KeyR&DProgram of China (2018YFC0604703); the Natural Science Foundation of Shandong Province (ZR2018MEM008) and the National High Technology Research and Development Program of China (SS2015AA031901) .

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Publication Dates

• Publication in this collection
  21 May 2021
• Date of issue
  2021

History

• Received
  23 Nov 2020
• Reviewed
  26 Mar 2021
• Accepted
  27 Apr 2021