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Gradient-distributed ZTAp-VCp/Fe45 as new anti-wear composite material and its bonding properties during composite casting

  • Lei Fan , Chun Hu , Neng Yang , Xingshuai Fan , Jie Cheng EMAIL logo and Xiangming Li
Published/Copyright: May 26, 2023
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Science and Engineering of Composite Materials
From the journal Science and Engineering of Composite Materials Volume 30 Issue 1

Abstract

In this article, gradient-distributed VCp-ZTAp/Fe45 composites were prepared by vacuum sintering, and three-body abrasive wear experiments were carried out to investigate its anti-wear performance. The composite casting of VCp-ZTAp/Fe45 was investigated by using the finite element method and experiments, and the bonding between the Fe45 substrate and 35SiMnCrMoNi steel was fully investigated. Results show the in situ formation of VCp in the VCp-ZTAp/Fe45 composite matrix during vacuum sintering. The anti-wear property of the VCp-ZTAp/Fe45 composite is ca. 7 times that of Hardox450 and NM450 and ca. 8 times of 30SiMn. There forms a solid metallurgical bonding between the Fe45 matrix of VCp-ZTAp/Fe45 and 35SiMnCrMoNi steel, with a ca. 80 μm thickness of the bonding area during the composite casting.

Keywords: composite material; abrasive wear; finite element method

1 Introduction

Coal is the most widely used fossil energy at present, but the harsh working conditions of coal mining equipment make the key components (such as shearer pick seat and scraper conveyor) suffer from serious abrasion [1,2,3,4]. The resulting frequent maintenance and parts replacement caused huge economic losses. In order to improve the wear resistance of key components in coal mining equipment, it is necessary to develop new materials that have improved wear resistance. Particle-reinforced iron-based composites have received extensive attention from researchers due to high mechanical strength and good wear resistance [5,6,7,8]. The common reinforcing phase particles mainly include titanium carbide (TiC) [9,10], aluminum oxide (Al2O3) [11,12], vanadium carbide (VC) [13], tungsten carbide (WC) [14] and zirconia toughened alumina (ZTA) [15,16,17,18]. Dong et al. [9] prepared TiC-reinforced iron matrix composites and studied the anti-wear performance by the two-body abrasive wear tests. Results show that when the load is 1.5 kg, the relative wear resistance of TiC-reinforced iron matrix composites is 2.67 times that of pure gray cast iron. Li et al. [15] prepared ZTAp–Fe composites and found the ZTAp well combines with iron matrix and the ZTAp–Fe composite material has good compressive strength. Our previous research [19] proves the bonding properties of ZTAp with iron matrix could be improved by treating the surface of ZTAp with nickel plating. Research from Wang et al. [17] show the ZTAp–Fe composites have better impact wear resistance than pure iron matrix materials. Vanadium (V) is easy to react with carbon (C) to form VCp at high temperatures, and the ratio of V to C decreases with the increase of carbon element in the reaction process [20,21]. The VC content was also proved to affect the microstructure and the mechanical properties of VC/Fe matrix composites [22]. Besides, the influences of the sintering temperature on the densification of Fe–VC composites was also investigated during the in-situ synthesis process [23]. However, the research on particle-reinforced iron matrix composites mainly focuses on that using a single reinforcing phase particle. Few reports could be found on that using the mixed reinforcing phase particles or the wear-resistance of the composite materials.

Casting is an important process in the preparation of key components of large coal mining equipment. Therefore, it is of great importance to develop the casting technique in order to facilitate the application of particle-reinforced iron-based composite materials in industries. Tayal et al. [24] used composite casting technology to join pure Mg and Al alloy (A356) together and proved that the graph theory approach was an effective tool to evaluate the optimal parameters for the composite casting process. Bakke et al. [25] achieved a high-quality bond between cast Al alloy (A356) and pure Cu through a gravity composite casting. Tensile tests showed that the bimetallic interface obtains a maximum ultimate tensile strength of 90.8 MPa. Fan et al. [26] studied the pouring temperature on the microstructure of Mg/Al steel bimetallic castings prepared by the composite casting process, and results showed that the interfacial bonding is the most stable when the casting temperature is 780°C. The investigations on composite casting nowadays are generally done by experiments, and there is little work done by theoretical simulation combined with experiments, which is of great significance in revealing the formation mechanism of the interface transition zone after composite casting.

In this work, the vacuum sintering was used to prepare the VCp-ZTAp/Fe45 composite material, and the strengthening mechanism was investigated. In order to make the bond of the cladding metal and the VCp-ZTAp/Fe45 composite material more stable during composite casting, the VCp-ZTAp/Fe45 composite is gradient-distributed, with an upper layer of VCp-ZTAp/Fe45 and a lower layer of Fe45 matrix. The three-body abrasive wear experiment was carried out on the VCp-ZTAp/Fe45 composites to study their anti-wear property. Finite element method (FEM) was used to study the surface temperature change and internal temperature field distribution of the Fe45 matrix layer in composite casting. The interface between the VCp-ZTAp/Fe45 composites and the cladding material was analyzed microscopically. Combining the simulation and experimental methods, the bonding between the VCp-ZTAp/Fe45 and the cladding layer was revealed.

2 Experimental and simulation

This article describes the preparation of VCp-ZTAp/Fe45 composites and the characterization of the materials. The three-body abrasive wear performance of VCp-ZTAp/Fe45 composites was studied based on the key components of coal mine general mining equipment which are subjected to wear conditions during operation.

2.1 Preparation and characterization of VCp-ZTAp/Fe45 composites

Gradient VCp-ZTAp/Fe45 composites were prepared by vacuum sintering method. The metal matrix is Fe45 powder with an average particle size of 50 μm. The morphology of Fe45 powder and ZTAp is shown in Figure 1(a) and (b), respectively. The element content of ISA is shown in Table 1. The in-situ self-generation technology was used to introduce VCp as the second reinforcing phase. The ISA powder was added with ferrovanadium powder (element content shown in Table 1) and carbon black powder. The mass ratio of the mixed ferrovanadium powder to carbon black powder was 1:8.5. The mixed powder was added to the Fe45 powder at a mass fraction of 5%. Planetary ball milling machine was used to mix the powder. The milling time was 1.5 h and the mass ratio of ball to material was 6:1. The powder compact was prepared by adding Fe45 powder and the mixed powder into the mold sequentially and was molded using a tablet press (C0514–PP-60S, Tianjin Science and Technology Products, China). Then, the powder compact was vacuum sintered using a carbon tube sintering furnace (ZT-50-22Y, Shanghai Chenhuan Science Technology Corp. Ltd., China) and the sintering temperature was 1,180°C. The scheme of VCp-ZTAp/Fe45 composite material preparation process is shown in Figure 2. The crystal properties of VCp-ZTAp/Fe45 composites were analyzed by Cu Kα radiation using an X-ray diffractometer (XRD, D2 PHASER, Bruker corporation, USA). The operating voltage was 40 kV, the scanning speed was 0.02°/s, and the scanning range was 20–90°. The microstructure of the VCp-ZTAp/Fe45 composites was observed using a scanning electron microscope (SEM, S3400N, Hitachi, Japan). The images provided in the article are secondary electron images.

Figure 1 Raw material morphology: (a) Fe45 powder; (b) ZTA particle.
Figure 1

Raw material morphology: (a) Fe45 powder; (b) ZTA particle.

Table 1

Element content of Fe45, ferrovanadium, and 35SiMnCrMoNi powder

(wt%) C Si Mn Cr Mo Ni Fe B V Al
Fe45 0.098 0.57 — 15.5 — 0.065 79.2 1.33 — —
Ferrovanadium 0.40 2.00 — — — — 46.00 — 50.00 1.5
35SiMnCrMoNi 0.36 0.50 1.14 1.10 0.21 0.59 96.10 — — —
Figure 2 Preparation processes of the VCp-ZTAp/Fe45 composites.
Figure 2

Preparation processes of the VCp-ZTAp/Fe45 composites.

2.2 Three-body abrasive wear test

Hardox450, 30SiMn and NM450 steels were selected as the control samples. The three-body abrasive wear tests were conducted using a rubber grinding wheel abrasive wear tester (MLG-130, Zhangjiakou Chengxin Testing Equipment Manufacturing Co., Ltd., China). The experiment followed the ASTM-G65 dry sand rubber wheel abrasive wear test standard [27]. Quartz sands with a particle size of 40–70 mesh were used as abrasive, and the sand flow rate was ca. 340 g/min. The diameter of the rubber wheel was 178 mm, and the rotation speed was 200 rpm. The load was 130 N, and the total experimental time was 10 min. Each experiment was repeated at least five times to avoid the influence of other disturbing factors.

After the three-body abrasive wear experiment, the samples were ultrasonic cleaned in ethanol and dried in vacuum. The wear rate was evaluated by the volume loss, which was weighted using an electronic balance (FA2004B, Sahanghai Yueping Instrument Co., Ltd, China) before and after the wear test. The surface topography of the samples and the wear test were observed by SEM.

2.3 Fe45/35SiMnCrMoNi composite casting

During the composite casting, Fe45, instead of VCp-ZTAp/Fe45, was used as the preform (core) to simplify the composite casting process, and the casting molten steel was 35SiMnCrMoNi (element content shown in Table 1). The size of the preform was 40 mm × 13 mm × 13 mm, and the size of the casting was 100 mm × 67 mm × 40 mm. Sand molds were made of industrial water glass sand. The pouring temperature was 1,650°C. After composite casting, the samples were cut, ground, polished and corroded to expose the interface between the preform and the cladding layer. The bonding condition of the interface between preform and cladding was observed using SEM, and the built-in energy dispersive analyzer was used to study the elemental distribution.

The composite casting process was also simulated using the finite element analysis software (ProCAST), including the whole process of filling and solidification. The entire process of filling and curing follows the following assumptions [28].

  1. The incoming liquid metal is evenly distributed only on the inlet of the centrifugal flow part to simulate the smooth filling process of the channel flow part.

  2. The liquid metal is an incompressible Newton fluid.

  3. The inlet is on the inside surface, with one component of inlet velocity parallel to the rotation axis and the other component vertical to the rotation axis.

The continuity and Navier–Stokes equations employed for the filling process of the two parts are as follows:

Continuity equation [29]:

(1) D = ∂ u ∂ x + ∂ v ∂ y + ∂ w ∂ z .

Navier-Stokes equation [30]:

(2) ∂ ( ρ ϕ ) ∂ t + ∇ ⋅ ( ρ V ̲ → ϕ ) = ∇ ⋅ ( μ ∇ ϕ ̲ ) + S u − ∇ P ,

where ρ is the density, ϕ is the velocity component, t is the time, V ̲ → is the velocity vector, μ is the dynamic viscosity, S u is the source of the momentum, and p is the pressure. For heat transfer behavior during steel solidification, the following equations are employed [31].

(3) ρ c d T d t = ∇ ⋅ ( k ∇ T ) + Q ̇ ,

where c is the specific heat, T is the temperature, k is the thermal conductivity, and Q ̇ is an internal power source.

The critical simulation parameters were set as follows: the initial temperature of the model was 25°C, the pouring temperature was 1,650°C, and the pouring time was 20 s. The preform and the cladding layer formed a metal–metal interface, and the heat transfer coefficient was set to 3,000 W/(m2 K). The core material and the sand mold formed a metal–sand interface, and the heat transfer coefficient was set 500 W/(m2 K). The model used the mesh with a 2 mm tetrahedron. The heat dissipation method of the external end-face of the sand mold shell and the end-face of the riser was air cooling, which was set to air cooling (FilmCo = 10, T = 20°C).

3 Results and discussions

This article provides an in-depth analysis of the phase and microstructure of VCp-ZTAp/Fe45 composites. Results show the presence of α-(Fe–Cr–Ni), (Fe, Cr)2B, (Fe, Cr)7C3, Al2O3, ZrO2 and VC in the VCp-ZTAp/Fe45 composite. Among them, α-(Fe–Cr–Ni), (Fe, Cr)2B and (Fe, Cr)7C3 are the main phases of Fe45. Al2O3 and ZrO2 are the main constituent phases of ZTAp. The comparison of the wear performance of VCp-ZTAp/Fe45 composites and Hardox450, 30SiMn and NM450 steels is also shown in this article.

3.1 Phase and microstructure of VCp-ZTAp/Fe45 composites

The following chemical reactions (equations (4)–(9)) may occur during the vacuum sintering of VCp-ZTAp/Fe45, and the standard Gibbs free energy for each reaction could also be calculated [32]. Figure 3 shows the calculated standard Gibbs free energies of Cr7C3, V2C, VC and Fe2B in the temperature range of 273 K < T < 1,458 K. It is obvious all the calculated results are negative, indicating all the earlier chemical reactions may occur spontaneously during the vacuum sintering process.

(4) 7 Cr + 3 C = Cr 7 C 3 ; ∆ G T = − 181 . 167 − 0 . 025465 T ,

(5) 2 V + C = V 2 C; ∆ G T = − 147 . 277 + 0 . 002362 T ,

(6) V + C = VC; ∆ G T = − 102 . 100 + 0 . 00958 T ,

(7) 2 Fe + B = Fe 2 B; ∆ G T = − 71 . 128 + 0 . 004749 T ,

(8) 4 Cr + C = Cr 4 C; ∆ G T = − 17 . 870 − 0 . 0005 T ,

(9) 3 Cr + 2 C = Cr 3 C 2 ; ∆ G T = − 20 . 07 − 0 . 00285 T .

Figure 3 Thermodynamic calculation results of the standard Gibbs free energy.
Figure 3

Thermodynamic calculation results of the standard Gibbs free energy.

Figure 4 presents the XRD results of the VCp-ZTAp/Fe45 composites. Results show the presence of α-(Fe–Cr–Ni), (Fe, Cr)2B, (Fe, Cr)7C3, Al2O3, ZrO2 and VC in the VCp-ZTAp/Fe45 composite. Among them, α-(Fe–Cr–Ni), (Fe, Cr)2B and (Fe, Cr)7C3 are the main phases of Fe45. Al2O3 and ZrO2 are the main constituent phases of ZTAp. Combined with the thermodynamic calculation results, it can be seen that during the vacuum sintering process, the C element in the raw material reacts with the V element to form a new VC phase. No V2C could be observed in the material because V2C has more carbon vacancies, and V2C is unstable and forms the more stable VC when carbon atoms are sufficient in our experiments. Cr3C2 and Cr4C traces could not be detected in XRD results as well, and this might be due to the small absolute value of ΔG in equations (5) and (6), which means the formation tendency of Cr3C2 and Cr4C is less within the calculated temperature range.

Figure 4 X-Ray diffraction (XRD) results of the VCp-ZTAp/Fe45 composite.
Figure 4

X-Ray diffraction (XRD) results of the VCp-ZTAp/Fe45 composite.

The interface of the ZTAp and the Fe45 matrix in the VCp-ZTAp/Fe45 composites was observed using SEM, as shown in Figure 5. ZTAp well combines with the matrix material and forms a clear and uniform interface. The thermal expansion coefficient of Fe (ca. 10.8 × 10−6/°C) [33] is larger than that of ZTAp (ca. 7.8 × 10−6/°C) [34]. During the sintering cooling process, ZTAp is under compressive stress, while the Fe45 matrix is under tensile stress, which forms thermal expansion dislocation strengthening. In this way, ZTAp and the Fe45 matrix form a solid bonding. The VCp uniformly distributes around the grain boundaries of the Fe45 matrix, as indicated in the yellow square areas in Figure 5. The measured element constitution is V, C, Fe and Cr. The shape of VCp is spherical [23], which could be seen in the Insert in Figure 5.

Figure 5 Microstructure of VCp-ZTAp/Fe45 composite by scanning electron microscopy (SEM).
Figure 5

Microstructure of VCp-ZTAp/Fe45 composite by scanning electron microscopy (SEM).

3.2 Anti-wear property of VCp-ZTAp/Fe45 composites

The volume loss of VCp-ZTAp/Fe45 composites and Hardox450, 30SiMn, NM450 steels was measured after the three-body abrasive wear tests; the result of which is shown in Figure 6. Results show that Fe45 alone shows improved anti-wear performance compared with Hardox450, 30SiMn and NM450 steels. The volume loss of the VCp-ZTAp/Fe45 composites is ca. 1/7 that of Hardox450 and NM450, and ca. 1/8 that of 30SiMn, indicating that the anti-wear property of VCp-ZTAp/Fe45 composites is obviously higher than the conventional steel materials.

Figure 6 The volume loss measured in the three-body abrasive wear tests.
Figure 6

The volume loss measured in the three-body abrasive wear tests.

The wear morphologies of Hardox450, 30SiMn, NM450 steels and VCp-ZTAp/Fe45 composites were observed using SEM, as shown in Figure 7. The wear morphologies of Hardox450, 30SiMn and NM450 steels are very similar, and there are a lot of furrows and pits on their surfaces. Comparatively, the number of furrows and pits on the surface of Fe45 is less, which is in line with the volume loss results in Figure 6. Figure 7(e) shows the surface morphology of the VCp-ZTAp/Fe45 composite, and an obvious height difference could be observed between the ZTAp and the Fe45 matrix. Based on the good anti-wear property of Fe45, it could be seen that the ZTAp does not detach from Fe45 after the wear tests, indicating that the bonding between the ZTAp and Fe45 is quite solid. The enlarged image of the ZTAp (area in indicated in the red square in Figure 7e) is shown in Figure 7(f). There are a lot of scratches on the surface of the ZTAp particles because of their protrusion above the matrix, and scratches could be observed on it. Some debris could also be observed around the ZTAp due to its rupture during abrasion. However, only a few furrows and pits could be observed on the surface of the Fe45 matrix, due to its good anti-wear property.

Figure 7 Surface morphology observed using SEM after the three-body abrasive wear tests of (a) Hardox450; (b) 30SiMn; (c) NM450; (d) Fe45; (e) VCp-ZTAp/Fe45 and (f) ZTAp.
Figure 7

Surface morphology observed using SEM after the three-body abrasive wear tests of (a) Hardox450; (b) 30SiMn; (c) NM450; (d) Fe45; (e) VCp-ZTAp/Fe45 and (f) ZTAp.

Combining the results in Figures 5 and 6, the further enhanced anti-wear performance of VCp-ZTAp/Fe45 composite may be partly due to the existence of VCp. For three-body abrasive wear, the wear volume is positively correlated with the reciprocal (1/H) of the material hardness, as is indicated in equation (10) [35]. V is the wear volume, W is the normal force, α is the angle of attack, tan α ̅ is the average of tan α , and H is the material hardness. The VCp plays a role in dispersion strengthening [36] and improves the hardness of the matrix. Therefore, there are fewer traces of furrows and pits in the matrix of the VCp-ZTAp/Fe45 composite, and its anti-wear property is thereby improved.

(10) V = 2 W tan α ¯ π H .

Figure 8 shows the three-body abrasive wear mechanism of VCp-ZTAp/Fe45 composites. At the initial stage of wear, the abrasives micro-plough the VCp-ZTAp/Fe45 composites under the combined action of tangential stress and normal stress, as shown in Figure 8(b). The matrix area of the VCp-ZTAp/Fe45 composite material all suffers from violent wear, and ZTAp suffers from comparatively gentle wear because the hardness of ZTAp is much higher than that of the Fe45 matrix [17]. ZTAp will gradually protrude from the matrix and form a certain slope with the matrix (as shown in Figure 7f). Therefore, the ZTAp shares large parts of the abrasive force and protects the substrate, reducing the micro-ploughing on the substrate, as shown in Figure 8(c). With the abrasion time prolonged, cracks of ZTAp also appear at the interface between the Al2O3 and ZrO2 phases, forming some debris, as shown in Figure 8(d).

Figure 8 Three-body abrasive wear mechanism of VCp-ZTAp/Fe45. (a) Initial surface; (b) early wear stage; (c) middle wear stage; (d) final wear stage.
Figure 8

Three-body abrasive wear mechanism of VCp-ZTAp/Fe45. (a) Initial surface; (b) early wear stage; (c) middle wear stage; (d) final wear stage.

3.3 Fe45/35SiMnCrMoNi bonding property during composite casting

In order to investigate the compatibility between the VCp-ZTAp/Fe45 composite material and the 35SiMnCrMoNi (common material for coal mining equipment) during the composite casting, Fe45 was selected as the core and 35SiMnCrMoNi was selected as the cladding layer. The material thermophysical parameters such as thermal conductivity, specific heat, density, latent heat, and enthalpy may change with the temperature [37–40]. During the casting process, the thermophysical parameters directly affect the heat transfer and temperature changes, and therefore, they need to be calculated before the temperature field calculation. Since the material involves the release of the latent heat of solidification during the phase transition process, the fraction solid, the solidus and liquidus of the material are also important for simulation calculations. By using ProCAST software, the solidus of Fe45 is calculated 1,202°C, and the liquidus of Fe45 is 1,350°C. The solidus of 35SiMnCrMoNi calculated is 1,131°C and the liquidus of 35SiMnCrMoNi is 1,490°C. The thermal conductivity of Fe45 and 35SiMnCrMoNi increases gradually with the increased temperature. When the phase transition occurs, the enthalpy suddenly changes. The enthalpy of Fe45 changes abruptly at 1,200–1,350°C, and the enthalpy of 35SiMnCrMoNi changes abruptly at 1,200–1,500°C, which corresponds to the release of the latent heat of fusion of Fe45 and 35SiMnCrMoNi during the phase transformation process. The change in material density is the main cause of material solidification shrinkage. With the decreased temperature, the molecular motion of the material is less active, and the density increases. The density of Fe45 and 35SiMnCrMoNi decreases abruptly between 1,200–1,350 and 1,200–1,500°C, respectively due to the solidification process of the materials.

The assembly of the core (Fe45) and cladding layer (35SiMnCrMoNi) is shown in Figure 9, a cross-sectional view of which is also shown in this figure to make it clear to the readers. The temperature field and fraction solid distribution of the Fe45/35SiMnCrMoNi interface are shown in Figure 10. The temperature of the Fe45 is obviously affected by the high temperature of molten 35SiMnCrMoNi during the casting process. The temperature of the upper surface and upper corners of the Fe45 shows the most obvious increase, and the high-temperature area gradually spread from the top to the center and the bottom of Fe45. At 6 s, the molten metal completely wraps the Fe45. At 12 s, the temperature of the upper area of Fe45 reaches the solidus temperature. At the same time, the fraction solid of the Fe45 decreases, and the upper area is at a solid–liquid coexistence state. At 16 s, sand mold filling is complete, and the top of Fe45 reaches the liquidus temperature. At 50 s, the whole Fe45 core reaches the liquidus temperature, and the molten 35SiMnCrMoNi steel is at liquid or solid–liquid coexistence state. Due to the good diffusion properties of the liquid phase, atoms at the interface of Fe45 and 35SiMnCrMoNi could easily exchange to form a metallurgical bond at this moment.

Figure 9 The assembly of the core (Fe45) and the cladding layer (35SiMnCrMoNi).
Figure 9

The assembly of the core (Fe45) and the cladding layer (35SiMnCrMoNi).

Figure 10 (a) Temperature and (b) fraction solid of core (Fe45) and cladding layer (35SiMnCrMoNi).
Figure 10

(a) Temperature and (b) fraction solid of core (Fe45) and cladding layer (35SiMnCrMoNi).

The interface after casting was observed by SEM, as shown in Figure 11(a). The structure of the cladding layer (35SiMnCrMoNi) is tempered sorbite, and the Fe45 matrix of the VCp-ZTAp/Fe45 composite material is mainly ferrite. Fe45 and 35SiMnCrMoNi are well combined, forming a clear and tight interface with a thickness of ca. 80 um. Neither pores nor other defects could be observed, indicating the bonding formed is solid. The elemental distribution along the bonding interface is shown in Figure 11(b). Elements such as Fe, C and Si evenly distribute along the bonding area. The content of Cr gradually decreases from the left part (Fe45) to the right part (35SiMnCrMoNi), indicating that the bonding formed between the two materials is the metallurgical bond. In a word, all the above results prove that in the process of pouring and solidification of 35SiMnCrMoNi molten steel on Fe45 matrix within 50 s, the elements completely interdiffuse at the interface, forming a robust interfacial bonding. The results show that the substrate of the VCp-ZTAp/Fe45 composite material has good compatibility with the 35SiMnCrMoNis steel during the composite casting process.

Figure 11 Interface morphology of Fe45/35SiMnCrMoNi after composite casting. (a) SEM image of the interface; (b) EDS results of the interface.
Figure 11

Interface morphology of Fe45/35SiMnCrMoNi after composite casting. (a) SEM image of the interface; (b) EDS results of the interface.

4 Conclusions

In order to improve the anti-wear performance of key components of mining equipment and its service life, gradient-distributed vanadium carbide-zirconia toughened alumina particles reinforced iron matrix (VCp-ZTAp/Fe45) composites were prepared by vacuum sintering in order to obtain the good anti-wear performance. Three-body abrasive wear experiments were carried out to investigate its anti-wear performance. Besides, the composite casting process of Fe45 (core) and 35SiMnCrMoNi (cladding material) was investigated by using the FEM, and the bonding property was studied.

Results show that the VCp-ZTAp/Fe45 composite material has excellent anti-wear properties than the mining wear-resistant steel currently used. The wear volume of VCp-ZTAp/Fe45 composite is ca. 1/7 of Hardox450 and NM450 and ca. 1/8 of 30SiMn. The spherical VC particle disperses along the grain boundaries of Fe45 and forms the dispersion strengthening of the matrix, thus improving its mechanical strength. The three-body abrasive wear mechanism of VCp-ZTAp/Fe45 composites was also revealed. The results from the FEM calculation of the casting process of Fe45/35SiMnCrMoNi indicate that both materials can be in liquid or solid–liquid coexistence state at the same time during the casting process within 50 s. At this time, the elements of Fe45 and 35SiMnCrMoNi can interdiffuse well at the interface of the Fe45/35SiMnCrMoNi to form a robust metallurgical bonding, with a ca. 80 um thickness of the bonding area. All these results prove the as prepared VCp-ZTAp/Fe45 composite material is quite promising in the application as the anti-wear material for mining equipment and has good compatibility with other steel during the composite casting process.

Acknowledgements

The work was supported by the State Key Laboratory of Tribology in Advanced Equipment (No. SKLTKF20B11 and SKLTKF21A01), Fundamental Research Funds for the Central Universities (No. 2021YQJD21 and 2021XJJD01), and Natural Science Foundation of Beijing Municipality (No.22C10149). The authors thank Dr. Yang Qin from China University of Mining and Technology-Beijing for the constructive suggestions in three-body abrasive wear tests.

  1. Conflict of interest: Authors state no conflict of interest.

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Received: 2022-11-15
Revised: 2023-03-29
Accepted: 2023-04-16
Published Online: 2023-05-26

© 2023 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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https://doi.org/10.1515/secm-2022-0200
Keywords for this article
composite material; abrasive wear; finite element method
Creative Commons
BY 4.0

Articles in the same Issue

  1. Regular Articles
  2. Effects of cellulose nanofibers on flexural behavior of carbon-fiber-reinforced polymer composites with delamination
  3. Damage mechanisms of bismaleimide matrix composites under transverse loading via quasi-static indentation
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