648 lines
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648 lines
30 KiB
Plaintext
## Page 1
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251
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Vol. 46, No. 2 (2024) 251-259, DOI: 10.24874/ti.1531.08.23.11
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Tribology in Industry
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www.tribology.rs
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Comparative Analysis of Wear Behavior of High
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Entropy Alloy (TiVNbCrAl) and Ti-based
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Conventional Alloy (TiNbCrCoAl)
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Dheyaa F. Kadhima,*
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aDepartment of Mechanical Engineering, University of Thi-Qar, 64001, Iraq.
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Keywords:
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Pin on disk tribometer
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Tribological performance
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High entropy alloys
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High-temperature wear behavior
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A B S T R A C T
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This research examined the relationships between processing, structure, and
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property at both room temperature and increased temperature for two BCC
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high entropy alloy (TiVNbCrAl) and Ti-based conventional alloy (TiNbCrCoAl)
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prepared using standard arc melting. Both alloys have been determined to
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have the BCC single-phase solid solution structure.To investigate the hardness
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and tribological behavior and processes at room temperature and above,
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microindentation and sliding wear experiments were undertaken. Both alloys
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display comparable friction behavior when sliding at room temperature, with
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an average steady-state coefficient of friction (COF) of 0.6. When sliding
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temperatures rise to 302 °C, the average COF for HEA (TiVNbCrAl) has
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decreased to a lowest value of ~0.4 due to the creation of a persistent
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tribochemical layer made of Nb and Cr oxides amid the sliding surfaces, which
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lowers COF. Whereas, COF for Ti-based conventional alloy remains at higher
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values of ~0.65. Mechanistic wear analyses revealed that the formation of
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tribofilms with low interfacial shear strength inside the wear tracks was the
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cause of this. The tribofilms were identified to be mostly constituted by multielement solid solution oxides, such as Ni2O5, Cr2O3, and NiO2, according to
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Raman spectroscopy. The Vickers microharness values for Ti-based
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conventional alloy is about 365±4 HV. Whereas, for high entropy alloy is about
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572±12 HV due to the solid solution strengthening.
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© 2024 Published by Faculty of Engineering
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* Corresponding author:
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Dheyaa F. Kadhim
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E-mail: dheyaa.kadhim@utq.edu.iq
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Received: 8 August 2023
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Revised: 10 October 2023
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Accepted: 1 November 2023
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1. INTRODUCTION
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Since the Bronze Age, alloying has been pursued as
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a way to strengthen metals. Traditionally, a single
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element is used as the base material, and solute
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atoms alter stress fields to prevent mobility of
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dislocation and reinforce the material, however
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this typically reduces ductility [1]. One of the
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pertinent difficulties in materials science is the
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development of innovative alloys with superior
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mechanical, tribological, and corrosion properties
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all at once. Over the past 20 years, these techniques
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have been utilized successfully to the design of
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novel materials under the theory of high-entropy
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alloys (HEAs) [2,3]. Alloys with a minimum of five
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components and component concentrations
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ranging from 5 to 35 at.% fall under this category
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of materials. A stable thermodynamically RESEARCH
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## Page 2
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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252
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substitutional solid mixture with the starting bcc,
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fcc, or hcp structure is a distinctive feature of HEAs
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[4-7]. Using this method, we can create new alloys
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that have a Exceptional balance of toughness,
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elasticity, hardness, and resistance to wear.
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Outstanding corrosion resistance is ensured by the
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large concentration of evenly dispersed passive
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oxide-forming components, such as Cr. These
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characteristics of HEAs make them superior to
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conventional iron alloys as materials with multiple
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uses [8-10].
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Wear and friction are significant engineering
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issues categorized as their reactions to a tribosystem. However, it is critical to manage material
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wear in order to lower maintenance costs and
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avoid material failure in service for aero-engine
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applications. For steady operations and a long
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lifespan, wear-resistant materials must be
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created. Because of the lattice distortion effect
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and high entropy mixing that supplies the alloy
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strength and inhibits plastic distortion and
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dislocation developments, high entropy alloys
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have recently come into use. These alloys and
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their distinguishing features have attracted
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research interest [11,12].
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Numerous high entropy alloys with promising
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properties have been developed as of late, including
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the high strength (BCC) AlCoCrFeNi and NbMoTaV
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alloys as well as the high wear-resistant
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Al0.2Co1.5CrFeNi1.5Ti and Co1.5CrFeNi1.5Ti
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alloys. Additionally, it was noted that the ability to
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corrode of the multi-component Cu0.5NiAlCoCrFeSi
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alloy is higher than that of the standard 304-
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stainless steel [13]. A high-entropy bulk metallic
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glasses (BMG) that may be plastically deformed at
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normal temperature includes CuCoNiCrAlFeTiV,
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FeCrMnNiCo, NbMoTaWV, CoCrFeNiCu, and
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AlCoCrFeNi [14].
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In this study, two TiNbCrCoAl Conventional and
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TiVNbCrAl high entropy alloys were manufactured.
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Microstructure, topological and tribological
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properties were studied. Wear is considered
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significant occurrence in many mechanical
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components. However, little data on the tribological
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nature of TiVNbCrAl high entropy alloy never been
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reported in the literature to best of our knowledge.
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Therefore, we conducted hardness and
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unidirectional sliding wear tests on both
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conventional and high entropy alloy to examine the
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wear behavior and friction mechanisms during
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room and elevated temperatures.
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2. EXPERIMENTAL METHODS
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Two BCC alloys—a conventional alloy (TiNbCrCoAl)
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and a high entropy alloy (TiVNbCrAl)—with either V
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or Co were investigated. By using an arc-melting and
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casting process, ingots were created. The specimens
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had been finished and ground using conventional
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metallographic techniques for microstructural
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characterisation. Acetone was used to etch the
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specimens such that tiny precipitates and grain
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boundaries could be seen. The wear behavior of both
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alloys was examined using a Falex ISC-200 (Falex
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corporation) pin on disk tribometer in accordance
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with ASTM G99 [15]. In laboratory air with a 40%
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relative humidity, the sliding coefficient of friction
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was determined at ambient and higher temperatures
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(102°C and 302°C). The high entropy alloy samples
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were put to the test by sliding unidirectionally against
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Si3N4 ball counter faces with 3.175 mm and 23 GPa
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diameter and hardness. For all tests, the sliding speed
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was 8.5 mm/s, and the standard load was 0.25 N. The
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Hertzian contact stress was decided to be less than
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the alloys' yield strength at 0.6 GPa based on these
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measurements. For all testing, the overal distance of
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sliding was 200 m. For the sake of reproducibility, at
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least two measurements were taken for each high
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entropy alloy. An optical microscope was used to take
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pictures of the Si3N4 counter faces and the worn
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surfaces of the high entropy alloy samples after each
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test. To measure roughness and wear track depths, a
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stylus profilometer (Veeco Dektak 150 Profilometer)
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was employed. To obtain the cross sectional worn
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area, at least seven traces were obtained across each
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wear track. According to Archard's equation, the
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wear factor/rate is determined by dividing the
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eliminated volume loss over the total sliding distance
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and applied force. The volume removal can be
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determined by dividing the worn surface's area by
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the circular wear track's circumference, assuming
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uniform wear. Using a Rigaku Ultima III X-ray
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diffractometer with radiation parameters of 30 kV,
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20 mA, a Cu K anode, and a scanning speed of 2
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degree/minute, crystal structures were found. An
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FEI-Nova 200 dual beam electron microscopy
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instrument was used for the analysis of the
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microstructural development during the frictional
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procedure and the wear surface. Using a 532 nm laser
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wavelength, Raman spectrometer was utilized to
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identify the tribo-chemical phases on the worn
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surfaces. Using Shimadzu Vickers hardness
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measuring devices with a load of 9.8 N and an
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acquisition duration of 10 seconds, roomtemperature micro hardness evaluations were made.
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## Page 3
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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253
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3. RESULTS AND DISCUSSION
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3.1 Microstructural and structural analysis
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Figure 1 displays the Ti-based conventional
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alloy XRD pattern. As can be seen, a distinct
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peak of the BCC phase was found at room
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temperature for typical alloys.
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Fig. 1. XRD pattern of Ti-based conventional alloy.
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In contrast, one set of peaks that correspond to
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either a B2 structure or a mixture of the B2 and
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BCC can be found in the high entropy alloy seen
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in Figure 2.
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Fig. 2. XRD pattern of high entropy alloy.
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In addition, Figure 3 backscattered SEM image
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shows that both alloys have interdendritic and
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dendritic morphologies. Table 1 provides the
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standard alloy chemical ingredients. It should
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be noticed that Ti predominates in this alloy,
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followed by Nb. At room temperature, Ti24Nb-3Al has only one BCC phase, according to
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Inamura et al [16]. The martensitic phase was
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discovered to exist in Ti-18Nb-3 Al and Ti20Nb-3Al alloys at ambient temperature [16].
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According to Guo's recommendation, the
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predicted valence electron concentration (VEC)
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value for conventional alloy is 4.44, which
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indicates that the alloy should include a single
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phase [17], and XRD results are in agreement
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with this. The chemical compositions for high
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entropy alloy determined from the EDS data are
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shown in Table 1. Additionally, the AlNbTiV
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HEA contains a dendritic BCC phase, according
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to N.D. Stepanov et al [18]. Nb (24.8 at.%) was
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abundant in the dendritic sections, while Al
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(27.6 at.%) enhanced the interdendritic region.
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The valence electron concentration (VEC),
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which has been used to determine the phase
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stability HEAs. VEC is defined by:
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𝑉𝐸𝐶 = ∑𝐶𝑖(𝑉𝐸𝐶)𝑖
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𝑛
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𝑖=1
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where (VEC)i is the value for contuent elements.
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Fig. 3. SEM images of (a) Ti-based conventional and
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(b) high entropy alloy.
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a- Conventional
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b- HEA
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## Page 4
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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254
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VEC was used to explain why the AlNbTiV HEA
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produced solid solution instead of intermetallic
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mixtures. It was discovered that the production
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of solid solution on the AlNbTiV high entropy
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alloy requires VEC= 4.25 [18]. Senkov further
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said that the NbTiZrV alloy has A2 phase.
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However, BCC and Laves phases were present in
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CrNbTiVZr and CrNbTiZr alloys [19]. According
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to Guo's proposal, the multi-component alloy
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should include a single phase because the
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estimated VEC value for the alloy is 4.6. [17], and
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XRD results are in agreement with this. As a
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result, there is only one BCC solid solution
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without intermetallics.
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Table 1. Composition of Ti-based conventional and high entropy alloy by SEM/EDS performed results.
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Alloy Element Cr Co Ti Nb Al V
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HEA At. % 21 18.88 18.68 21.65 20.05
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Conventional At. % 5.2 6.19 68.28 12.46 7.87
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3.2 Micro hardness analysis
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The Vickers micro hardness pattern along the
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surface of both Ti-based conventional alloy and
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high entropy alloy in the as-cast form is shown
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in Figure 4.
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Fig. 4. Microhardness trends of Ti-based conventional
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and high entropy alloy.
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The average hardness value for the conventional
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alloy 365±4 HV. The high entropy alloy, on the
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other hand, is made up of almost equiatomic
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components. The alloy only has one solid BCC
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solution. Its Vickers hardness is a respectable
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572±12 HV. In addition, The high hardness of
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HEA can be linked to formation of BCC phase
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which is enhanced by the addition of Ti which
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considered as bcc stabilizer [20]. Moreover, Al
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serves to maintain the BCC [21]. The alloy's
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mechanical attributes are comparable to those
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of AlNbTiV, which possess microhardness value
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of 440 HV [18]. Besides, the Al atomic size is
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considered to be larger than that of other alloy
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elements. This leads to lattice distortion and
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promote solid solution strengthening , thus
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overall HEA strength will be enhanced [22].
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Moreover, Vanadium plays a vital role in rising
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the hardness of HEA as reported by Dong et al
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[23]. They studied the effect of vanadium on the
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properties of NiCoAlCrFe HEA. They found that
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the Vickers harness increased from HV534 to
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HV648.8 with increasing the vanadium and the
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solid solution strengthening was the main
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reason behind the rise in hardness values.
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3.3 Wear behavior and tribology properties
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3.3.1 Wear behavior at 27°C
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Figure 5 shows the friction behaviour of high
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entropy alloy (TiVNbCrAl) and Ti-based
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conventional alloy (TiNbCrCoAl) at room
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temperature. It can be noticed that both alloys
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behave in similar manner and both alloys had
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the same value of coefficient of friction (COF) of
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about ~0.6
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Fig. 5. Friction curve of conventional and high entropy
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alloy at 27°C.
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## Page 5
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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255
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3.3.2 Wear behavior at 102°C
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The friction behavior of Ti-based conventional alloy
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and HEAat 102°C is shown in Figure 6. In comparison
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to ambient temperature, the friction is greater. The
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friction behavior also exhibits a lot of noise. For the
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Ti-based conventional alloy, the COF increased from
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~0.6 to about ~0.8 before reaching steady state.
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Contrarily, the COF of the high entropy alloy began at
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0.8 and decreased through a number of transitions
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before reaching the steady state COF of ~0.6.
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Fig. 6. Friction curve of conventional and high entropy
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alloy at 102°C.
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3.3.3 Wear behavior at 302 °C
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Figure 7 depicts the friction behavior of a
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conventional and high entropy alloy 302°C. The
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HEA has a steady state COF of roughly ~0.4 due to
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the presence of Ni and Cr oxides which lowers the
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friction (which will be discussed later in Raman
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section). However, the COF of conventional alloy at
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steady state was roughly~ 0.6.
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Fig. 7. Friction curve of conventional and high entropy
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alloy at 302°C.
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3.4 Analysis of worn surfaces
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3.4.1 Scanning electron microscope of wear scars
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According to the morphologies shown in Figures
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8 and 9, both alloys suffer from severe abrasive
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wear, which is evident in the form of plowed
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grooves and visible plastic deformation.
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(a) (b) (c)
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(d) (e) (f)
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Fig. 8. SEM wear track images of Ti-based conventional alloy (a, b, c) and the corresponding Si3N4 pin surface
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optical images (d, e, and f).
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## Page 6
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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256
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(a) (b) (c)
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(d) (e) (f)
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Fig. 9. SEM wear track images of high entropy alloy (a, b, c) and the corresponding Si3N4 pin surface optical images
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(d, e, and f).
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The Si3N4 counter face's harsh asperities and
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the consolidated wear detritus seem to have
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generated the plastic deformation that caused
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the majority of the material loss in
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conventional alloy to occur through oxidation
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wear. However, the oxide particle-induced
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micro-cutting may also be a factor in the
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volume loss. Additionally, adhesive wear
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occurred, as shown by the material transfer and
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the creation of cracks and oxide spots from
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delamination. The adhesion theory states
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[24,25], When two contacting surfaces are
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moved against one another, The pairing
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surfaces' irregularities cling to the other side.
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When sliding, the worn materials will migrate
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between the two layers. The break off
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frequently occurs in the softer material. It may
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be predicted that material is largely transferred
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from conventional alloy to the Si3N4 ball because
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the hardness of the Si3N4 counter face is higher
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than that of conventional alloy. The surface
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oxidation of reactive Ti serves as evidence of
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the presence of oxides at the worn surface [26].
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According to the worn scar morphology of the
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multi-component alloy, the test was conducted
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under light wear circumstances. Slight
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adhesive, oxidation, and spalling of the
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attached material are the main mass removal
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methods. It may be assumed that during the
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sliding wear test, volume is transferred from
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the multi-component alloy to the counter face
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since the multi-component alloy is softer than
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the Si3N4 counter face [26]. Improved hardness
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and decreased COF of the multi-component
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alloy at 102 °C are compatible with the ocular
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observation of less wear when compared to
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traditional alloy.
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3.4.2 Oxides determination of wear scars
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According to the literature-based Raman
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spectroscopy database [27-32], inside the wear
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tracks, As illustrated in Figure 10, it can be
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ascertained that the extremely little wear scars
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contains a variety of metal oxides, including
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Nb2O5, NbO2, Cr2O3, and TiO2. According to certain
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reports [33-34], metal oxides like Cr2O3 and
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Nb2O5 can lower the friction coefficient and are
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effective at preventing alloy fracture . Based on
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the Raman spectra of the two alloys, it has been
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determined that the inclusion of NbO2 and Nb2O5
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in the high entropy alloy (TiVNbCrAl) wear track
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also contributes to a reduction in friction and
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wear as compared to Ti-based conventional alloy
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(TiNbCrCoAl), which do not contain a large
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quantities of such tribochemical components.
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## Page 7
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Dheyaa F. Kadhim, Tribology in Industry Vol. 46, No. 2 (2024) 251-259
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257
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Fig. 10. Raman spectra for Ti-based conventional alloy
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and high entropy alloy wear tracks at RT.
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3.4.3 Calculations of wear rates
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The wear rate of HEA and Ti-based conventional
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alloys were calculated to be 1.12E-07
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(mm3/N.m), and 5.55E-08 (mm3/N.m),
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respectively. The degrees of hardness are
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respectively 365±4 and 572±12. Intermittent
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generation of the wear debris is possible.
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Additionally, the Ti-based conventional alloy,
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which wears out considerably more quickly than
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high entropy alloy, has a deep wear track.
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Nevertheless, the high entropy alloy with the
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lowest RT friction coefficient has a little greater
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wear rate. Its slightly decreased hardness is
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probably to blame for this.
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4. CONCLUSION
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The as-cast microstructures and wear behaviors
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of two high entropy alloy (TiVNbCrAl) and Tibased conventional alloy (TiNbCrCoAl) were
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investigated. Some important conclusions can
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be drawn depending on the wear test performed
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with pin on disk tribometer at room and
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elevated temperatures.
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1. The main phase in Ti-based conventional alloy
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(TiNbCrCoAl) and high entropy alloy
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(TiVNbCrAl) is BCC structure.
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2. The averaged hardness value for Ti-based
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conventional alloy is about 365±4 HV. Whereas,
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for high entropy alloy is about 572±12 HV, that
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is superior to that of Ti-based conventional
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alloy. This can be attributed the Presence of Ti
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and V elements which stabilizes the bcc
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structure and enhance the Vickers hardness.
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3. Ti-based conventional Alloy (TiNbCrCoAl) has
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wear rate of 1.12E -07 (mm3/N.m), at RT. It
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demonstrates the worst tribological qualities
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when combined with increased friction.
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4. Due to its relatively ductile BCC solid solution
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and B2ordered phase, High Entropy Alloy
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(TiVNbCrAl) has outstanding overall
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tribological properties at low and high
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temperatures. The formation of an ongoing
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tribochemical coating between the sliding
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surfaces made of Nb and Cr oxides, which helps
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lower the friction coefficient. Due to its greater
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Vickers hardness of 57212 HV, it demonstrated
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a low rate of wear of 5.55 E-08 (mm3/N.m) at RT,
|
||
outperforming Ti-based Conventional Alloy.
|
||
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