Friction & Wear

Wear-Fatigue Behavior of Ni88 P11.78 Co0.12 Fe0.10 and Ni80.55 Cr15.25 B4.20 Metallic Glasses During Rubbing Against an Eccentric Rotating Ceramic Roller

[+] Author and Article Information
C. Serrar

 Laboratoire de Thermodynamique et Surfaces des Matériaux Département de Physique, Université Mentouri Constantine 25100, Algeriaserrarcherif@yahoo.fr

P. Guiraldenq

 Département Sciences et Techniques des Matériaux et des Surfaces (STMS) LTDS (UMR-CNRS5513) Ecole Centrale de Lyon, BP 163 Ecully – 69131, CEDEX, Francepierre.guiraldenq@orange.fr

J. Tribol 134(4), 041603 (Aug 23, 2012) (11 pages) doi:10.1115/1.4007218 History: Received February 01, 2011; Revised June 04, 2012; Published August 23, 2012; Online August 23, 2012

The wear-fatigue rupture of Ni88 P 11.78 Co0.12 Fe0.10 (NiP) and Ni80.55 Cr15.25 B4.20 (NiCrB) glasses prepared by planar–flow casting have been studied using a test under simultaneous constant and cyclic loading generated by an eccentric rotation ceramic antagonist. For better apprehending the phenomena related to the structural state changes of samples before and after tests, structural characterization by x-ray diffraction, mechanical characterization by measuring Vickers microhardness (HV 0.1) and chemical composition by X-ray photoelectron spectroscopy (XPS) analysis have been carried out on as-quenched and worn dull side ribbons. Rupture surfaces, in S–N curves, have been measured by scanning electron microscope. Wear-fatigue contact tests consist to impose, simultaneously, a traction strain and cyclic normal stresses which generate traction, compression, rolling, bending and shearing. All results obtained from the two selected glasses (NiP and NiCrB) are systematically compared with those of a nickel pure crystalline foil (Ni). We evaluate mainly the wear mechanism, the mode and the typical rupture surface observed in NiP, NiCrB and Ni specimens. We specify the conditions of obtaining these rupture surfaces which often present in smooth plane, veining and “chevrons” patterns. All results show a great wear and fatigue resistance for the two metallic glasses compared to Ni. The NiCrB wear resistance is superior to that of NiP, while the difference in their fatigue limit is not clearly distinct. The reasons for the differences in wear and fatigue behavior will be discussed in relation to the metallic glass thermal stability, chemical composition, microhardness and surface rupture topography.

Copyright © 2012 by American Society of Mechanical Engineers
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Figure 1

Wear-fatigue test machine

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Figure 2

Schematic representation of thicknesses (surface rupture and as–quenched specimens) of the Ni, NiP, and NiCrB specimens, tested in wear–fatigue conditions, up to their rupture at 7.5 N and 20 N, respectively

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Figure 3

Lost wear volume (mm3 N-1 ) for wear-fatigue tests: as a function of applied loads, P, varying from 1 to 39 N (a) and of number of elapsed cycles (at 20 and 7.5 N) (b), for NiP, NiCrB and Ni tested specimens, respectively

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Figure 4

XPS analysis from dull side (DS) surface to the bulk of the as-quenched: NiP glass (a), NiCrB glass (b) and (c). Same analysis done on NiP worn surface tested at 20 N for 1.8 × 105 cycles (d). Profile of element composition is very perturbed in the subsurface of ribbon. It shows an oxygen peak, which is more emphasized for NiP specimen; this peak disappears after ∼1.8 × 105 cycles of wearing.

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Figure 5

Scanning electron micrograph of typical worn surface observed in NiP glass. roughness surface in as-quenched state (a), for tested specimen at 20 N: surface accommodation by progressive elimination of roughness after ∼ 4 × 104 cycles (b), oxide film removal by superficial microcracking after ∼5 × 104 cycles (c), amorphous substrate is then worn: very small number of wear particles and grooving trace which are present on the worn surface and at the end of contact surface with roller, after ∼9.2 × 104 cycles (d)

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Figure 6

TEM micrograph observations of the shaped worn surface of a NiP glass specimens (a) and its selected area diffraction pattern (b). The tested NiP is obtained from lubricant wear–fatigue conditions at 20 N, after ∼6 × 105 cycles, the structure remains completely amorphous.

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Figure 7

SEM micrograph with a shift ∼10 deg, of the worn surface taken from a NiP specimen, tested in dry wear–fatigue conditions at 20 N, after ∼5.5 × 104 cycles. Many dendrite arms (crystallized particles) are seen on the worn surface.

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Figure 8

S-N curves of the specimens tested up to their final rupture, at variable initial loads P, from 1 to 40 N for NiP and NiCrB glasses and it varies from 1 to 15 N for Ni pure crystalline foil

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Figure 9

SEM micrograph of rupture surfaces, with a shift ∼35 deg, showing smooth and vein patterns, for NiP and NiCrB tested at 20 N up to final rupture after ∼6 × 105 cycles (a) and ∼8 × 108 cycles (b), respectively

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Figure 10

SEM micrograph, work with a shift ∼46 deg, of the typical fracture surface showing a chevron pattern form for the broken NiP glass specimens, loaded at 20 N, after ∼4 × 103 cycles. Tearing initiation and growth was occurred from notch defects which are located at the specimen edges.

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Figure 11

SEM micrograph, with a shift ∼40 deg, of the typical rupture surface of NiP glass specimen especially tested up to its rupture, at 35 N, after ∼1.2 × 105 cycles. A larger thickness of the vein pattern zone, with denser and greater long arms of veins can be observed.

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Figure 12

SEM micrograph, with a shift ∼45 deg, of the typical rupture surface of Ni pure crystalline foil tested up to rupture, at 7.5 N, after ∼4.5 × 105 cycles. Fatigue striations can be clearly seen.

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Figure 13

SEM micrograph, with a shift ∼45 deg, of the typical rupture surface of NiP glass specimen tested up to rupture, at 20 N, after ∼2 × 105 cycles. Cracking initiation and growth are occurred at the worn contact surface center.

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Figure 14

Microhardness (HV 0.1) measured near the central zone of worn contact surface, as a function of elapsed cycles, of Ni, NiP and NiCrB specimens, tested up to their rupture, at 7.5 N and 20 N, respectively




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