Development of a simple ‘temperature versus sliding speed’ wear map for the sliding wear behaviour of dissimilar metallic interfaces
Development of a simple ‘temperature versus sliding speed’ wear map for the sliding wear behaviour of dissimilar metallic interfaces
复制标题
DOI：
10.1016/j.wear.2005.06.008
复制
发表时间：
2006-05
期刊：
影响因子：
5
通讯作者：
I. Inman;S. R. Rose;P. K. Datta
中科院分区：
文献类型：
--
作者：
I. Inman;S. R. Rose;P. K. Datta
研究了 Nimonic 80A 与 Stellite 6（配合面）在室温和 750°C 之间、滑动速度为 0.314、0.654 和 0.905ms−1 时有限碎片滞留滑动磨损期间磨损行为的变化。在 0.314ms−1 时，由于源自 Stellite 6 的碎片转移和氧化到 Nimonic 80A 以及 Nimonic 80A 和 Stellite 6 磨损表面的分离，在所有温度下都观察到了轻微的氧化磨损。在室温到 450°C 之间，这些碎片大多以松散颗粒的形式存在（只有有限的压实），而在 510 到 750°C 之间，颗粒被压实并烧结在一起，形成耐磨保护“釉层”。在 0.654 和 0.905ms−1 时，仅在室温和 270°C 下（在 0.654ms−1 时也在 390°C 下）观察到由 Stellite 6 来源碎片的转移和氧化引起的轻度氧化磨损。在 390°C（450°C，0.654ms−1）及更高温度下，这种氧化物完全不存在，“金属与金属”接触导致中温严重磨损状态，以喷射金属碎片形式出现的损失几乎完全来自 Nimonic 80A。这次来自 Nimonic 80A 样品的氧化物碎片直到 570°C（630°C，0.654ms−1）才重新出现，然而，直到 690 和 750°C 才足以完全消除严重磨损。在 0.654 和 0.905ms−1 下，现在在 690 和 750°C 下防止严重磨损的氧化物往往不会在 Nimonic 80A 的表面上形成“釉”层，而是通过磨损支持持续的高磨损。这种磨蚀作用归因于 Nimonic 80A 来源的氧化物的较差的烧结特性，以及氧化物的流动性增加和驻留时间降低。收集的数据用于构建一个简单的磨损图，详细说明在室温至 750°C 之间的速度和温度下，滑动速度和温度对 Nimonic 80A 相对于 Stellite 6 滑动的磨损的影响。
The variation in wear behaviour during limited debris retention sliding wear of Nimonic 80A versus Stellite 6 (counterface) between room temperature and 750°C, at sliding speeds of 0.314, 0.654 and 0.905ms−1, was investigated. At 0.314ms−1, mild oxidational wear was observed at all temperatures, due to transfer and oxidation of Stellite 6-sourced debris to the Nimonic 80A and resultant separation of the Nimonic 80A and Stellite 6 wear surfaces. Between room temperature and 450°C, this debris mostly remained in the form of loose particles (with only limited compaction), whilst between 510 and 750°C, the particles were compacted and sintered together to form a wear protective ‘glaze’ layer. At 0.654 and 0.905ms−1, mild oxidational wear due to transfer and oxidation of Stellite 6-sourced debris was only observed at room temperature and 270°C (also 390°C at 0.654ms−1). At 390°C (450°C at 0.654ms−1) and above, this oxide was completely absent and ‘metal-to-metal’ contact resulted in an intermediate temperature severe wear regime—losses in the form of ejected metallic debris were sourced almost completely from the Nimonic 80A. Oxide debris, this time sourced from the Nimonic 80A sample, did not reappear until 570°C (630°C at 0.654ms−1), however, were insufficient to eliminate completely severe wear until 690 and 750°C. At both 0.654 and 0.905ms−1, the oxide now preventing severe wear at 690 and 750°C tended not to form ‘glaze’ layers on the surface of the Nimonic 80A and instead supported continued high wear by abrasion. This abrasive action was attributed to the poor sintering characteristics of the Nimonic 80A-sourced oxide, in combination with the oxides’ increased mobility and decreased residency. The collected data were used to compose a simple wear map detailing the effects of sliding speed and temperature on the wear of Nimonic 80A slid against Stellite 6, at these speeds and temperatures of between room temperature and 750°C.