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Series: ASM Failure Analysis Case Histories
Publisher: ASM International
Published: 01 June 2019
DOI: 10.31399/asm.fach.mech.c9001530
EISBN: 978-1-62708-225-9
... examined. Both samples were subjected to accelerated wear tests in a laboratory type pin-on-disk apparatus. During the tests, the bearing materials acted as pins, which were pressed against a rotating cast iron disk. The wear behaviors of both bearing materials were studied using weight loss measurement...
Abstract
This paper describes an investigation on the failure of a large leaded bronze bearing that supports a nine-ton roller of a plastic calendering machine. At the end of the normal service life of a good bearing, which lasted for seven years, a new bearing was installed. However the new one failed catastrophically within a few days, generating a huge amount of metallic wear debris and causing pitting on the surface of the cast iron roller. Following the failure, samples were collected from both good and failed bearings. The samples were analyzed chemically and their microstructures examined. Both samples were subjected to accelerated wear tests in a laboratory type pin-on-disk apparatus. During the tests, the bearing materials acted as pins, which were pressed against a rotating cast iron disk. The wear behaviors of both bearing materials were studied using weight loss measurement. The worn surfaces of samples and the wear debris were examined by light optical microscope, SEM, and energy-dispersive x-ray microanalyzer. It was found that the laboratory pin-on-disk wear data correlated well with the plant experience. It is suggested that the higher lead content ~18%) of the good bearing compared with 7% lead of the failed bearing helped to establish a protective transfer layer on the worn surface. This transfer layer reduced metal-to-metal contact between the bearing and the roller and resulted in a lower wear rate. The lower lead content of the failed bearing does not allow the establishment of a well-protected transfer layer and leads to rapid wear.
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Published: 01 January 2002
Fig. 26 Fatigue cracks in laboratory test specimens of (a) a steering knuckle made of ferritic ductile iron showing macroscopic features of a fatigue crack initiated at a sharp corner, and (b) a rotating bending fatigue specimen made of as-cast gray iron. Fatigue in this relatively brittle
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Published: 01 January 2002
Fig. 32 Transmission electron fractograph of aluminum alloy laboratory spectrum loading fatigue test. Striation spacing varies according to loading, which consisted of ten cycles at a high stress alternating with ten cycles at a lower stress. The fracture surface exhibits bands of ten coarse
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Published: 01 January 2002
Fig. 43 SEM view of laboratory fatigue fracture of a 70-30 nickel-copper alloy showing mixed intergranular and transgranular morphology. Source: Ref 24
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Published: 01 January 2002
Fig. 49 SEM view of fatigue striations in medium-density polyethylene, laboratory tested at 0.5 Hz with maximum stress 30% of the yield strength. Crack growth is upward in this view. Original magnification 200×. Source: Ref 4
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Published: 01 January 2002
Fig. 5 Typical carrying case for field and laboratory photographic equipment
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Published: 01 January 2002
Fig. 69 Internal oxidation of a nickel-chromium steel carburized in a laboratory furnace, showing both grain-boundary oxides and oxide precipitates within grains. 402×. Source: Ref 30
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Published: 01 December 1992
Fig. 1 Laboratory-fatigue-tested cross member sample 1, showing cracking progression from internal fillet-welded diaphragm through channel side wall at location indicated by arrow.
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in Intergranular Stress-Corrosion Cracking of Carbon Steel Pipe Welds in a Kamyr Continuous Digester Equalizer Line
> Handbook of Case Histories in Failure Analysis
Published: 01 December 1992
Fig. 4 Scanning electron micrograph of the laboratory-induced fracture. Dimples are characteristic of microvoid coalescence, a ductile form of fracture.
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in Hot Corrosion of Stainless Steel Grate Bars in Taconite Indurators
> Handbook of Case Histories in Failure Analysis
Published: 01 December 1992
Fig. 6 Results of laboratory hot corrosion (cyclic) tests on HH steel coupons for 100h. (a) and (b) Coupons corroded undersulfate and sulfate-chloride loading, respectively (c) and (d) Corrosion morphology undersulfate and sulfate-chloride loading, respectively.
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in Failure Analysis of Fire Tube Sleeve of Heater Treater
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 5 External view of failed specimen as received in laboratory
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in Hot Cracking in Inductively Bent Austenitic Stainless Steel Pipes
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 9 Scanning electron microfractograph of crack forced open in laboratory (see Fig. 7 ). Evidence of liquation cracking. Formerly molten low-melting grain boundary phases bridging between grains
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in Hot Cracking in Inductively Bent Austenitic Stainless Steel Pipes
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 10 Scanning electron microfractograph of crack forced open in laboratory (see Fig. 7 ). Fracture surface was etched for 2 min with “V2A etchant” at 80 °C. Evidence of formerly molten low-melting eutectic phases, probably a carbide eutectic, on grain boundaries ( arrows )
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in An Environmentally Assisted Cracking Evaluation of UNS C64200 (Al–Si–Bronze) and UNS C63200 (Ni–Al–Bronze)
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 5 ASB tested in laboratory air ( a ) intergranular fracture, ( b ) intergranular fracture showing slip band activity (HTP-8)
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in An Environmentally Assisted Cracking Evaluation of UNS C64200 (Al–Si–Bronze) and UNS C63200 (Ni–Al–Bronze)
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 6 Polished cross section of ASB specimen tested in laboratory air (HTP-2) showing bifurcated out-of-plane crack growth of after some amount of in-plane MVC fracture
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in An Environmentally Assisted Cracking Evaluation of UNS C64200 (Al–Si–Bronze) and UNS C63200 (Ni–Al–Bronze)
> Handbook of Case Histories in Failure Analysis
Published: 01 December 2019
Fig. 11 NAB RSL fracture surfaces in a laboratory air (MVC), b seawater (MVC), and c seawater + ammonia (IG). Fatigue precrack is located at bottom
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Published: 15 January 2021
Fig. 26 Fatigue cracks in laboratory test specimens. (a) Steering knuckle made of ferritic ductile iron showing macroscopic features of a fatigue crack initiated at a sharp corner. (b) Rotating-bending fatigue specimen made of as-cast gray iron. Fatigue in this relatively brittle gray iron
More
Image
Published: 15 January 2021
Fig. 32 Transmission electron fractograph of aluminum alloy laboratory spectrum loading fatigue test. Striation spacing varies according to loading, which consisted of ten cycles at a high stress alternating with ten cycles at a lower stress. The fracture surface exhibits bands of ten coarse
More
Image
Published: 15 January 2021
Fig. 43 Scanning electron microscope view of laboratory fatigue fracture of a 70-30 nickel-copper alloy showing mixed intergranular and transgranular morphology. Source: Ref 26
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in Thermomechanical Fatigue—Mechanisms and Practical Life Analysis
> Failure Analysis and Prevention
Published: 15 January 2021
Fig. 7 Typical thermomechanical fatigue (TMF) waveforms used in laboratory testing. (a) In-phase TMF. (b) Out-of-phase TMF. Image (b) adapted from Ref 6 , with permission from Elsevier
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