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A. NAGODE et al.: STRUCTURAL AND THERMODYNAMIC ANALYSIS OF WHISKERS ON THE SURFACE... REFERENCES [1] N. Arab, M. Rahimi Nezhad Soltani, Journal of Applied Chemical Research, 9 (2009), 13-23. [2] M. Gojić, J. Črnko, M. Kundak, L. Kosec, Kovové Materiály, 41 (2003), 158-166. [3] M. Bizjak, A. Zalar, P. Panjan, B. Zorko, B. Praček, Applied Surface Science, 253 (2007), 3977-3981. [4] A. Nagode, G. Klančnik, H. Schwarczova, B. Kosec, M. Gojić, L. Kosec, Engineering Failure Analysis, 23 (2012) 1, 82-89. [5] J. Tušek, D. Klobčar, Journal of Mechanical Engineering, 50 (2004) 2, 94-103. [6] I. Budak, M. Soković, M. Barišić, Measurement, 44 (2011) 6, 1188-1200. [7] D. Klobčar, L. Kosec, B. Kosec, J. Tušek, Engineering Failure Analysis, 20 (2012) 1, 43 – 53. [8] M. Medved, V. Malenković, E. Dervarič, Technics Technologies Education Management, 6 (2011) 2, 247-255. [9] G. Kosec, A. Nagode, I. Budak, A. Antić, B. Kosec, Engineering Failure Analysis, 18 (2011) 1, 450-454. [10] F. Tholence, M. Norell, Oxididation of Metals, 69 (2008), 13-36. [11] B. Schmid, N. Aas, R. Ødegård, Oxidation of Metals, 57 (2002), 115-130. [12] R. L. Higginson, G. Green, Corrosion Science, 53 (2011), 1690-1693. [13] J. W. Kim, J.W. Choi, D.B. Lee, Metals and Materials International, 11 (2005), 131-134. [14] A. Ivanič, S. Lubej, R. Rudolf, I. Anžel, Science and Engineering of Composite Materials, 18 (2011) 3, 181-186. [15] J. Robertson, M.I. Manning, Materials Science and Technology, 5 (1989), 741-753. [16] M. B. Lin, C. Jeng, A.A. Volinsky, Oxidation of Metals, 76 (2011), 161-168. [17] A. T. Dinsdale, SGTE Data for Pure Elements, Calphad 15 (4) (1991), 317-425. [18] I. Ansara, SGTE Substance Database (2000). [19] B. Sundman, Journal of Phase Eguilibrium, 12 (1991), 127-140. [20] M. Selleby, B. Sundman, Calphad 20 (1996), 381-392. Note: The responsible translator for English language is Urška Letonja, MOAR, Podgora, Slovenia. 14 METALURGIJA 52 (2013) 1, 11-14
P. MALATYŃSKA, J. GŁOWNIA CARBON CONTENT INFLUENCE ON THE PERITECTIC REACTION PATH IN STAINLESS STEELS P. Malatyńska, J. Głownia, AGH University of Science and Technology, Kraków, Poland METALURGIJA 52 (2013) 1, 15-18 ISSN 0543-5846 METABK 52(1) 15-18 (2013) UDC – UDK 669.146.536.42.669.141.25=111 Received – Prispjelo: 2012-03-21 Accepted – Prihvaćeno: 2012-07-30 Original Scientifi c Paper – Izvorni znanstveni rad An important role for the peritectic reaction path in castings of stainless steel play small changes in a carbon content (e.g. from 0,02 to 0,06 % C), at maintaining constant chromium and nickel values. An infl uence of the carbon content on the peritectic reaction stages constitutes the subject of studies. The calculations of the steel solidifi cation pathways in the four-component system, of a constant chromium and nickel content of 18 % and 9 % – respectively and of various carbon content from 0,01 to 0,06 %, were performed. It was proved by means of the PANDAT program that the carbon concentration increases the Cr segregation and thereby changes the solidifi cation path under actual conditions. Key words: peritectic reaction, stainless steel, carbon content, segregation, simulation of solidifi cation. INTRODUCTION Investigations of the behaviour of the Fe-Cr18-Ni9 system during the peritectic reaction occurrence were performed by means of the PANDAT program. Regardless of several studies concerning the peritectic reaction [1 – 8] it is still a not well known effect. In order to understand better the processes occurring during this reaction several calculations of the system, allowing the visualisation of this change, were performed. This reaction is of an essential meaning in modern casting, since it is considered to be the cause of surface defects such as cracks and deformations, especially in thin casting walls. An occurrence of longitudinal cracks on casting surfaces is related to volumetric changes and fractions of ferrite and austenite phases, while transverse cracks to the formation of austenite grains [1]. The peritectic reaction [1 – 4] described many times, divides the peritectic change into three stages: the main reaction, phase transformation and solidifi cation. Mechanisms of the reaction and transformation were characterised in detail by H. Kerr [4]. Investigations of the solidifi cation of austenitic Fe- Cr-Ni steels will allow differentiating four solidifi cation forms, which depend on the initial phase and on further transformations in the solid phase [5]. The total solidifi - cation of the regular face-centred cubic phase, fcc, is called the A type, while the AF type [6] starts the solidifi cation process of the primary fcc phase, up to the fi nal stage of the eutectic reaction (fcc + bcc). The solidifi cation period of the primary body-centred cubic phase, bcc, up to the end of the eutectic reaction (bcc + fcc) is called the FA type. The total solidifi - cation of the bcc phase is marked as the F type. The total solidifi cation of the regular face-centred cubic, fcc (A type), phase depends on nickel, which stabilises this phase, whereas in case of the regular body-centred cubic, bcc (F type), phase chromium is the stabilizing element. For the A and AF solidifi cation types, at the primary solid phase growing, chromium contained in the alloy enriches interdendritic liquid causing an occurrence of the eutectic reaction (fcc + bcc) in the fi nal solidifi cation stage. The bcc phase is contained in the interdendritic zones of the formed eutectic in the retained, different morphology. For the FA and A solidifi cation types the interdendritic liquid is enriched in nickel, which causes the eutectic reaction occurrence (bcc + fcc), and the formed microstructure consists of the bcc phase dendrites surrounded by the fcc phase [6]. EXPERIMENTAL PART Calculations of the Fe-Cr-Ni system were performed for the constant chromium (18 %) and nickel (9 %) content, at the variable carbon content (from 0,01 to 0,06 %). The preformed examinations of the system were based on previous estimations made by Luoma [9], Hillert and Qiu [10] and Kundrad and Elliot [11]. The main aim of the investigations was the verifi cation in what way a small carbon content infl uences the fourcomponent system. The infl uence of chromium on the three-component Fe-Cr-Ni system in the peritectic reaction area is presented in Figure 1. This is the temperature range, specially considered in the paper. From among several calculated systems – solidifying within the peritectic reaction temperature – the following temperatures were selected for the analysis: 1 515 ˚C, 1 500 ˚C, 1 490 ˚C, 1 480 ˚C and 1 4750˚C. In the fi rst of these temperatures: 1 515 ˚C, for lower carbon 15
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R. KRUZEL, M. SULIGA THE EFFECT OF
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Figure 5 Process of rolling with up
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guarantees effi cient application o
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