Dry Sliding Wear Behaviour of Shot Peened TI6AL4V Alloys at Different Peening Times

Avcu, Yasemin Yıldıran; Yetik, Okan; Koçoğlu, Hürol; Avcu, Egemen; Sınmazçelik, Tamer

doi:10.12693/aphyspola.134.349

Cited by 8 publications

(7 citation statements)

References 14 publications

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“…The surface roughness significantly increased at the higher pressure since the crater formation resulted in an uneven surface (Figure 7b) [40]. Crater formation was the active deformation mechanism that modified the surface and changed the roughness via the formation of irregular valleys and peaks in the surface profile, similar to the results reported in the literature [4,25,55,56,63]. The influence of cover rate on the surface roughness was insignificant at the low pressure, whereas the [20], ECAP2 [77], HPT [31], ARB [17], CGP [71], HE [77], SP, homogenisation annealing.…”

Section: Surface and Subsurface Features Of Shot-peened Aa1050 Alloysupporting

confidence: 83%

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Modification of Surface and Subsurface Properties of AA1050 Alloy by Shot Peening

et al. 2021

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AA1050 Al alloy samples were shot-peened using stainless-steel shots at shot peening (SP) pressures of 0.1 and 0.5 MPa and surface cover rates of 100% and 1000% using a custom-designed SP system. The hardness of shot-peened samples was around twice that of unpeened samples. Hardness increased with peening pressure, whereas the higher cover rate did not lead to hardness improvement. Micro-crack formation and embedment of shots occurred by SP, while average surface roughness increased up to 9 µm at the higher peening pressure and cover rate, indicating surface deterioration. The areal coverage of the embedded shots ranged from 1% to 5% depending on the peening parameters, and the number and the mean size of the embedded shots increased at the higher SP pressure and cover rate. As evidenced and discussed through the surface and cross-sectional SEM images, the main deformation mechanisms during SP were schematically described as crater formation, folding, micro-crack formation, and material removal. Overall, shot-peened samples demonstrated improved mechanical properties, whereas sample surface integrity only deteriorated notably during SP at the higher pressure, suggesting that selecting optimal peening parameters is key to the safe use of SP. The implemented methodology can be used to modify similar soft alloys within confined compromises in surface features.

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Section: Surface and Subsurface Features Of Shot-peened Aa1050 Alloysupporting

confidence: 83%

“…SP was performed on the metallographically prepared AA1050 Al alloy samples with stainless-steel shots (diameter: 0.7-1.0 mm (type: Chronital S60), shot hardness: 450 HV) as detailed elsewhere [55,56]. Figure 1 shows the SP of AA1050 by highlighting some of the important parameters and dimensions.…”

Section: Shot Peening Processmentioning

confidence: 99%

Modification of Surface and Subsurface Properties of AA1050 Alloy by Shot Peening

et al. 2021

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“…Several surface treatments are employed to enhance the durability and longevity of titanium and its alloys. These techniques include heat treatment, shot peening [13], anodic plasma electrolytic oxidation [14], laser surface modification [15], and plasma-based ion implantation [16]. Additionally, the use of coatings such as diamond-like carbon films [17], PEO coatings [14], and graphene oxide [18] has been explored to enhance the wear resistance of Ti6Al4V alloy.…”

Section: Introductionmentioning

confidence: 99%

Effect of Oxidation Process on Mechanical and Tribological Behaviour of Titanium Grade 5 Alloy

Saier,

Esen,

Ahlatci

et al. 2024

Materials

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In this study, microstructural characterization, mechanical (tensile and compressive) properties, and tribological (wear) properties of Titanium Grade 5 alloy after the oxidation process were examined. While it is observed that the grey contrast coloured α grains are coaxial in the microstructures, it is seen that there are black contrast coloured β grains at the grain boundaries. However, in oxidised Titanium Grade 5, it is possible to observe that the α structure becomes larger, and the number and density of the structure increases. Small-sized structures can be seen inside the growing α particles and on the β particles. These structures are predicted to be Al-Ti/Al-V secondary phases. The nonoxidised alloy matrix and the OL layer exhibited a macrolevel hardness of 335 ± 3.21 HB and 353 ± 1.62 HB, respectively. The heat treatment increased Vickers microhardness by 13% in polished and etched nonoxidised and oxidised alloys, from 309 ± 2.08 HV1 to 352 ± 1.43 HV1. The Vickers microhardness value of the oxidised sample was 528 ± 1.74 HV1, as a 50% increase was noted. According to their tensile properties, oxidised alloys showed a better result compared to nonoxidised alloys. While the peak stress in the oxidised alloy was 1028.40 MPa, in the nonoxidised alloy, this value was 1027.20 MPa. It is seen that the peak stresses of both materials are close to each other, and the result of the oxidised alloy is slightly better. When we look at the breaking strain to characterise the deformation behaviour in the materials, it is 0.084 mm/mm in the oxidised alloy; In the nonoxidised alloy, it is 0.066 mm/mm. When we look at the stress at offset yield of the two alloys, it is 694.56 MPa in the oxidised alloy; it was found to be 674.092 MPa in the nonoxidised alloy. According to their compressive test properties, the maximum compressive strength is 2164.32 MPa in the oxidised alloy; in the nonoxidised alloy, it is 1531.52 MPa. While the yield strength is 972.50 MPa in oxidised Titanium Grade 5, it was found to be 934.16 MPa in nonoxidised Titanium Grade 5. When the compressive deformation oxidised alloy is 100.01%, in the nonoxidised alloy, it is 68.50%. According to their tribological properties, the oxidised alloy provided the least weight loss after 10,000 m and had the best wear resistance. This material’s weight loss and wear coefficient at the end of 10,000 m are 0.127 ± 0.0002 g and (63.45 ± 0.15) × 10−8 g/Nm, respectively. The highest weight loss and worst wear resistance have been observed in the nonoxidised alloy. The weight loss and wear coefficients at the end of 10,000 m are 0.140 ± 0.0003 g and (69.75 ± 0.09) × 10−8 g/Nm, respectively. The oxidation process has been shown to improve the tribological properties of Titanium Grade 5 alloy.

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“…Nonetheless, certain aspects remain to be clarified, including the mechanism of SP strengthening and the impact of SP parameters on the surface properties, wear resistance, fatigue resistance, and corrosion resistance of the workpiece. Avcu et al [19] proposed that shot peening significantly impacts the wear behavior of TI6AL4V alloy, yet they did not elucidate the mechanism by which shot peening enhances its wear resistance. Khun et al [20] found that increasing shot peening pressure enhanced the mechanical properties of SAE 1070 steel; however, they overlooked the potential influence of other shot peening parameters on its mechanical characteristics.…”

Section: Introductionmentioning

confidence: 99%

The effect of shot peening on the contact fatigue performance of C40 steel gears after laser surface melting

Lv,

Cui,

Sun

et al. 2024

Surf. Topogr.: Metrol. Prop.

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In this paper, shot peening (SP) was employed as a post-processing technique for the laser surface melted (LSMed) gear. The aim was to improve the contact fatigue performance of laser surface melting+shot peened (LSMSPed) gears. The microstructure, surface roughness, residual stress, microhardness of C40 steel gears before and after SP treatment were characterized using scanning electron microscopy, X-ray diffraction stress analyzer, contour measuring instrument, and hardness tester. Fatigue test of gear was carried out with a Forschungsstelle für Zahnräder und Getriebebau (FZG) testing machine. Following the laser surface melting (LSM) treatment, a molten layer was observed on the gear teeth surface. The experimental results indicated that SP induced a hardened layer with a certain thickness and plastic deformation on the surface of LSMed gears. Importantly, as the SP parameters increased, there's a corresponding reduction in both the average grain diameter and the maximum grain diameter. The reduction was most pronounced when the shot diameter reached its maximum value. It's worth noting that once the optimal threshold for SP parameters is surpassed, the residual compressive stress and microhardness on the LSMSPed gear surface do not exhibit a continuous growth trend. Furthermore, the rise in SP parameters resulted in a gradual increase in the surface roughness of LSMSPed gears, albeit to varying degrees. In light of the combined effects of grain refinement, residual compressive stress, microhardness, and surface roughness, the contact fatigue performance of LSMSPed gears improved with increasing SP parameters. Notably, when comparing the contact fatigue life of LSMed gears with that of LSMSPed gears, we observed a substantial enhancement. However, it's essential to highlight that when the shot diameter reaches its maximum value, the contact fatigue life of the LSMSPed gear, somewhat unexpectedly, decreased.

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Dry Sliding Wear Behaviour of Shot Peened TI6AL4V Alloys at Different Peening Times

Cited by 8 publications

References 14 publications

Modification of Surface and Subsurface Properties of AA1050 Alloy by Shot Peening

Modification of Surface and Subsurface Properties of AA1050 Alloy by Shot Peening

Effect of Oxidation Process on Mechanical and Tribological Behaviour of Titanium Grade 5 Alloy

The effect of shot peening on the contact fatigue performance of C40 steel gears after laser surface melting

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