【正文】 化物涂層 。磨損 率大大降低（ pt.圖 ）地區(qū)的內(nèi)部，在金相觀察，發(fā)現(xiàn)由 F?B 組成 ，并在較少 Fe2B程度 。 透過涂層會進一步向內(nèi)，磨損率增加在 F?B Fe2B 單界面圖（ pt. ），并成為該地區(qū)最低的高度有序的晶體構(gòu)成 Fe2B 單（ ）。 然后，磨損率增加的地區(qū)所構(gòu)成 Fe2B 單柱和 非滲硼鐵（ 5. 7），更有 甚 者，當(dāng)只有純粹的，軟鐵提交磨損圖（ ）。 指出的摩擦學(xué)行為的磨損率值圖進行報道。 圖 7 確認有必要向滲組件的表面處理程序，適用于消除外，抗差的硼化物涂層的一部分。 此外，這也可能解釋為什么一個有序和強硬的 Fe2B單是首選的高度強，一多相硼化物涂層，艱難，但是 在 FeBFe2B 高壓力的接口下 容易過早失效 。 4． 結(jié)論 多相硼化物涂層 提高鐵的性能， 結(jié)構(gòu)鋼是由一個 FeB 硼外層和內(nèi)層的 Fe2B 單 相 構(gòu)成的晶體與秩序的程度，這 與 外部表面不同深度所在地區(qū)不同。機械緊湊和耐磨性取決于此。 該涂層的磨損率高，最初都在滑動和磨料條件下， 因為 一個無序晶體外，薄，易碎層的存在 。 然后，磨損率下降是因為受了硼晶體排列第一的反抗，然后對 Fe2B 單 相 ，直到達成一項內(nèi)，非常緊湊的涂料地區(qū)的最低值由 Fe2B 單高度有序的晶體組成。 FeBFe2B 接口在高應(yīng)力狀態(tài)下使 硼化物的多相涂層摩擦學(xué)性能 大大降低 ，導(dǎo)致成核和裂紋沿界面擴張，并伴隨磨損碎片的形成。 通過厚度球的手段，縮孔和層的層的方法 對 磨損率進行了測量，被證明是評估不同深度的多相涂層耐磨性有效 途經(jīng)。 鳴謝 作者要感謝意大利冶金 協(xié)會 安德烈 .加萊西先生在微觀尺度磨損測試給予的支持。 參考文獻 [1] . Sinha, Boriding (boronizing), in: Heat Treating (Section: Surface Hardening of Steel), vol. 4, ASM Handbook, 1999, pp. 437–447. [2] R. ChatterjeeFischer, Boriding and diffusion metallizing, in: . Sudarshan (Ed.), Surface Modification Technologies, Marcel Dekker, New York, 1989, Chapter 8, pp. 567–609. [3] K. Bartsch, A. Leonhardt, Surf. Coat. Technol. 116–119 (1999) 386. [4] E. Rodr180。?guez Cabeo, G. Laudien, S. Biemer, . Rie, S. Hoppe, Surf. Coat. Technol. 116–119 (1999) 229. [5] A. K252。per, X. Qiao, . Stock, P. Mayr, Surf. Coat. Technol. 120 (2021) 87. [6] M. Carbucicchio, G. Palombarini, J. Mater. Sci. Lett. 6 (1987) 1147. [7] G. Palombarini, M. Carbucicchio, J. Mater. Sci. Lett. 6 (1987) 415. [8] . Rutherford, . Hutchings, J. Testing Eval. 3 (1997) 250. [9] . Staia, . Enriquez, . Puchi, . Lewis, M. Jeandin, Surf. Eng. 14 (1998) 49. [10] C. Martini, G. Palombarini, M. Carbucicchio, J. Mater. Sci. 39 (2021) 1. [11] C. Bindal, A. Erdemir, Appl. Phys. Lett. 68 (1996) 923. [12] R. Iakovou, L. Bourithis, G. Papadimitriou, Wear 252 (2021) 1007 外文原文 Sliding and abrasive wear behaviour of boride coatings C. Martini, G. Palombarini?, G. Poli, D. Prandstraller Abstract Polyphase boride coatings constituted by an inner layer of Fe2B and an outer layer of FeB were thermochemically grown on iron and medium carbon steel by a pack cementation process. The tribological behaviour of borided samples was investigated under both slidingand abrasion testing conditions. Considerably different values of wear rate were found in different regions of the coatings. The differences were explained on the basis of the crystallographic order of iron borides. The resistance to both types of wear was initially poor due to the presence on the coatings of a thin, friable layer constituted by disordered crystals. Then the resistance increased to a maximum value in regions constituted by pact, highly ordered crystals of Fe2B. The resistance to dry sliding of borided samples was better than that displayed by samples submitted to alternative surface treatments (. gas nitriding) and lower that that measured for aWC–Co hard metal coating. 169。 2021 Elsevier . All rights reserved. Keywords: Boriding。 Iron。 Steel。 Sliding wear。 Abrasive wear。 Preferred orientations。 Crystallographic order。 Tribotesting 1 Introduction A rapid expansion of activities in the field of surface modification techniques has been promoted by the increasing demand for materials with satisfactory resistance to wear, corrosion or both. In many applications, in fact, the inservice life of ponents is determined by surface properties. In the important field of thermochemical treatments of steels, based on diffusion of species such as carbon, nitrogen or boron, boriding is in a peculiar position. On one side, coatings constituted by iron borides thermochemically grown on steels generally display very high hardness, even in excess of 20 GPa, as well as high wear resistance [1,2]. Borided steel ponents display excellent performance in several tribological applications in the mechanical engineering and automotive industries. It is worth noting that the best results are obtained by pack cementation, . processes carried out using powder mixtures containing a boronising ponent (. B4C), an activator (usually KBF4) and eventually a diluent ponent added in order to control the boronising potential of the medium. However, as pared to gas phase treatments, industrial processes carried out with powders are: (i) more plicated, time consuming and expensive, and (ii) less suited to process control and automation, this situation hindering an adequate diffusion of boriding treatments. Efforts addressed to set up industrial gas boriding processes are in progress, with main problems concerning the control of both the processing conditions and position and porosity of the boride layers. In particular, a lack of knowledge is recognised about the interaction mechanisms between plasma and metal surface. As an example, boride coatings produced on two medium carbon steels by plasma assisted chemical vapour deposition at ～833K using a BCl3–H2 gaseous mixture diluted with Ar, were only few micrometers thick and contained in both cases a poorly adherent FeB layer [3]. On the other hand the wear performance of oil pump drive gears of an automotive engine, plasma borided in a similar gaseous mixture, were found parable with those obtained with pack boron cementation [4]. However, a postboriding heat treatment was required to obtain single phase layers, . coatings only constituted of the less hard but also less brittle iron boride Fe2B [4]. Attempts to substitute the boron halide and diborane boron precursors with anic precursors allowed to grow single Fe2B phase layers up to 10 _m thick on a medium carbon steel, any further growth being prevented by the unfavourable action displayed by carbon [5]. The tribological behaviour of these boride layers was evaluated only by parison with untreated samples. A lo