Features of Increasing the Wear Resistance of 90CrSi Tool Steel Surface under Various Electrophysical Parameters of Plasma Electrolytic Treatment
Abstract
:1. Introduction
2. Materials and Methods
2.1. Materials
2.2. Processing
2.3. Study of Morphology, Structure, and Element and Phase Composition
2.4. The Microhardness Measurement
2.5. Surface Roughness and Weight of Samples Measurement
2.6. Study of Tribological Properties
2.7. Determination of the Microgeometry Characteristics and Type of Violation of Friction Bonds during Friction
3. Results and Discussion
3.1. XRD Analysis of Samples Surface
3.2. SEM and EDX Analysis of Samples Cross-Section
3.3. Calculation of Nitrogen Diffusion Coefficients
3.4. Metallographic Analysis and Microhardness of Samples Cross-Section
3.5. Surface Morphology and Roughness
3.6. Tribological Properties of Samples
4. Conclusions
- 1.
- The possibility of increasing the hardness and wear resistance of the surface of 90CrSi tool steel by PEN followed by PEP has been demonstrated. The influence of electrophysical parameters of treatment on the composition, structure, morphology, and tribological properties of the steel surface was studied.
- 2.
- Structural changes in the surface of 90CrSi steel after PEN were revealed. Regardless of the polarity of the workpiece, an oxide layer with different phase composition and morphology is formed on the surface as a result of high-temperature oxidation of steel in electrolyte vapor. The formed oxide layers after APEN have a lower density compared to CPEN, which is explained by the process of anodic dissolution of steel and the formation of vacancies and pores. As a result of anodic dissolution, the surface roughness after APEN is reduced by 2.7 times. Free vacancies and pores in the oxide layer favor nitrogen diffusion: the diffusion coefficient during anodic treatment is 2.50 μm2/s, while after CPEN its value is 0.30 μm2/s. Consequently, after APEN, a nitride layer is formed under the oxide layer, which is not detected after CPEN. In both cases, martensite is formed as a result of quenching, and the microhardness increases to 1110–1120 HV. Due to incomplete martensitic transformation, retained austenite and cementite are identified in the surface layers.
- 3.
- It has been established that as a result of PEP, oxide layers having morphological inhomogeneities in the form of cracks, chips, and various irregularities are partially removed. The preservation of the nitride layer occurs only with PEP in a sulfate electrolyte for 1 min when surface passivation inhibits the electrochemical dissolution of steel. Under other PEP conditions, the nitride layer dissolves, and the roughness increases due to uneven etching. A denser oxide layer after cathodic treatment with PEP is removed more uniformly, which is accompanied by a decrease in roughness by 1.7 times. It was noted that under any PEP conditions after APEN and CPEN, the strengthened layer is preserved.
- 4.
- The features of the tribological behavior of the steel surface after processing at various PET parameters were determined. Wear of the surface of 90CrSi steel after APEN and subsequent PEP is accompanied by the formation of plastically deformed microvolumes of metal, which, upon repeated exposure, lead to the formation of wear particles and separation of the base material. In contrast, after CPEN and subsequent PEP, denser oxide layers take the load and, while slowly deteriorating, act as friction lubricants. This leads to the concentration of strains in a thin surface oxide layer and is reflected in a decrease in the relative penetration of the sample into the surface of the counterbody by 1.7 times after CPEN compared to the untreated sample, while after APEN, this figure decreases by 1.1 times. Similarly, the bearing capacity of a steel surface after CPEN followed by PEP is significantly higher than after APEN followed by PEP: in the first case, the Kragelsky-Kombalov criterion decreases by 1.4–1.5 times, and in the second case, it increases by 1.4–1.6 times compared to an untreated surface. The nature of wear is reflected in an increase in the friction coefficient by 1.3–1.5 times after APEN and subsequent PEP and in a decrease by 1.2 times after CPEN and two times after subsequent PEP. Despite significant differences in wear patterns, all modified samples showed an increase in wear resistance: 5–9 times after APEN followed by PEP, 16 times after CPEN, and up to 32 times after subsequent PEP. In all cases, the disruption of frictional bonds occurs through the plastic displacement of the material, and the wear mechanism is classified as fatigue wear during dry friction and plastic contact.
Author Contributions
Funding
Institutional Review Board Statement
Informed Consent Statement
Data Availability Statement
Acknowledgments
Conflicts of Interest
References
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Element | C | Cr | Si | Mn | Ni | S | P | Mo | W | V | Ti | Cu | Fe |
---|---|---|---|---|---|---|---|---|---|---|---|---|---|
wt.% | 0.85–0.95 | 0.95–1.25 | 1.2–1.6 | 0.3–0.6 | ≤0.4 | ≤0.03 | ≤0.03 | ≤0.2 | ≤0.2 | ≤0.15 | ≤0.03 | ≤0.3 | balance |
APEN | CPEN |
---|---|
2.50 μm2/s | 0.30 μm2/s |
Electrolyte for PEP | PEP Time (min) | Δm (mg) | Ra (μm) | Rz (μm) | μ | Tfr (°C) | Δmfr (mg) | h/r | Δ |
---|---|---|---|---|---|---|---|---|---|
Untreated | 1.00 ± 0.10 | 7.22 ± 0.51 | 0.361 | 51 | 28.40 | 0.080 ± 0.002 | 0.30 ± 0.01 | ||
APEN | 32.5 | 0.37 ± 0.07 | 2.12 ± 0.43 | 0.464 | 102 | 3.16 | 0.071 ± 0.001 | 0.42 ± 0.01 | |
NH4Cl + C3H8O3 | 1 | 25.8 | 3.19 ± 0.56 | 20.20 ± 3.03 | 0.532 | 111 | 5.29 | 0.072 ± 0.001 | 0.44 ± 0.01 |
2 | 67.4 | 3.84 ± 0.98 | 24.21 ± 4.91 | 0.506 | 104 | 5.07 | 0.078 ± 0.002 | 0.47 ± 0.01 | |
(NH4)2SO4 | 1 | 18.9 | 0.38 ± 0.05 | 1.96 ± 0.13 | 0.511 | 125 | 5.02 | 0.072 ± 0.001 | 0.48 ± 0.01 |
2 | 34.4 | 0.54 ± 0.24 | 5.42 ± 3.15 | 0.426 | 106 | 3.11 | 0.075 ± 0.002 | 0.45 ± 0.01 |
Electrolyte for PEP | PEP Time (min) | Δm (mg) | Ra (μm) | Rz (μm) | μ | Tfr (°C) | Δmfr (mg) | h/r | Δ |
---|---|---|---|---|---|---|---|---|---|
Untreated | 1.00 ± 0.10 | 7.22 ± 0.51 | 0.361 | 51 | 28.4 | 0.080 ± 0.002 | 0.30 ± 0.01 | ||
CPEN | 101 | 1.16 ± 0.11 | 6.94 ± 0.57 | 0.300 | 99 | 1.8 | 0.048 ± 0.001 | 0.21 ± 0.04 | |
NH4Cl + C3H8O3 | 1 | 54.1 | 1.13 ± 0.25 | 6.92 ± 0.91 | 0.309 | 92 | 1.6 | 0.048 ± 0.001 | 0.21 ± 0.04 |
2 | 82.1 | 0.68 ± 0.07 | 3.45 ± 0.26 | 0.263 | 79 | 1.8 | 0.046 ± 0.001 | 0.22 ± 0.04 | |
(NH4)2SO4 | 1 | 47.6 | 1.67 ± 0.32 | 9.80 ± 1.78 | 0.169 | 130 | 0.9 | 0.041 ± 0.001 | 0.20 ± 0.04 |
2 | 93.1 | 0.68 ± 0.16 | 3.56 ± 0.74 | 0.244 | 78 | 1.4 | 0.045 ± 0.001 | 0.22 ± 0.04 |
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Grigoriev, S.N.; Tambovskiy, I.V.; Mukhacheva, T.L.; Kusmanova, I.A.; Podrabinnik, P.A.; Khmelevsky, N.O.; Suminov, I.V.; Kusmanov, S.A. Features of Increasing the Wear Resistance of 90CrSi Tool Steel Surface under Various Electrophysical Parameters of Plasma Electrolytic Treatment. Metals 2024, 14, 994. https://doi.org/10.3390/met14090994
Grigoriev SN, Tambovskiy IV, Mukhacheva TL, Kusmanova IA, Podrabinnik PA, Khmelevsky NO, Suminov IV, Kusmanov SA. Features of Increasing the Wear Resistance of 90CrSi Tool Steel Surface under Various Electrophysical Parameters of Plasma Electrolytic Treatment. Metals. 2024; 14(9):994. https://doi.org/10.3390/met14090994
Chicago/Turabian StyleGrigoriev, Sergey N., Ivan V. Tambovskiy, Tatiana L. Mukhacheva, Irina A. Kusmanova, Pavel A. Podrabinnik, Nikolay O. Khmelevsky, Igor V. Suminov, and Sergei A. Kusmanov. 2024. "Features of Increasing the Wear Resistance of 90CrSi Tool Steel Surface under Various Electrophysical Parameters of Plasma Electrolytic Treatment" Metals 14, no. 9: 994. https://doi.org/10.3390/met14090994