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This paper presents a comprehensive study on the strain-induced martensitic transformation and reversion transformation of the strain-induced martensite in AISI 304 stainless steel using a number of complementary techniques such as dilatometry, calorimetry, magnetometry, and in-situ X-ray diffraction, coupled with high-resolution microstructural transmission Kikuchi diffraction analysis. Tensile deformation was applied at temperatures between room temperature and 213 K (À60°C) in order to obtain a different volume fraction of strain-induced martensite (up to~70 pct). The volume fraction of the strain-induced martensite, measured by the magnetometric method, was correlated with the total elongation, hardness, and linear thermal expansion coefficient. The thermal expansion coefficient, as well as the hardness of the strain-induced martensitic phase was evaluated. The in-situ thermal treatment experiments showed unusual changes in the kinetics of the reverse transformation (a¢ fi c). The X-ray diffraction analysis revealed that the reverse transformation may be stress assisted-strains inherited from the martensitic transformation may increase its kinetics at the lower annealing temperature range. More importantly, the transmission Kikuchi diffraction measurements showed that the reverse transformation of the strain-induced martensite proceeds through a displacive, diffusionless mechanism, maintaining the Kurdjumov-Sachs crystallographic relationship between the martensite and the reverted austenite. This finding is in contradiction to the results reported by other researchers for a similar alloy composition.

Dilatometry is the most commonly method of producing CCT diagrams and analyzing phase transformations during cooling (as well as transformations during heating) and it permits the real-time monitoring of the extent of reaction in terms of dimensional changes due to phase transformation. All modern dilatometers are fitted with computerised systems which collect dimensional change signals versus temperature to plot a dilatometric curve and also to calculate and plot the derivative of the relative dimensional change with respect to temperature. Unfortunately, elaborated by dilatometers manufacturers software, in many cases could lead to wrong interpretation of phase transformations during cooling.Keywords: dilatogram, derivative, phase transformations during cooling, software Dylatometria jest najczęściej stosowana technika badawczą przy tworzeniu wykresów CTPc i analizie przemian fazowych podczas chłodzenia oraz nagrzewania. Umożliwia również śledzenie na bieżąco postępu przemiany dzięki rejestracji zmian wymiarów próbki w trakcie przemiany. Wszystkie współczesne dylatometry są wyposażone w systemy komputerowe sterowania i akwizycji danych pomiarowych umożliwiające obserwację dylatogramu w trakcie chłodzenia czy nagrzewania jak również obliczenie i narysowanie po zakończeniu eksperymentu wykresu różniczki (pierwszej pochodnej) w funkcji temperatury. Niestety, fabryczne oprogramowanie w wielu przypadkach może prowadzić do błędnej interpretacji zjawisk podczas przemian fazowych w trakcie chłodzenia.

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The results of a microstructure and hardness investigations of the hypoeutectoid steels Mn-Cr-Ni, imitating by its chemical composition toughening steels, are presented in the paper. The analysis of the kinetics of phase transformations of undercooled austenite of steels containing different amounts of alloying elements in their chemical composition, constitutes the aim of investigations.Metallographic examinations were carried out on a Axiovert 200 MAT light microscope. Sections were etched with a 3% HNO 3 solution in C 2 H 5 OH.Dilatometric tests were performed using L78 R.I.T.A dilatometer. Using dilatometer the changes of elongation (∆l) of the samples with dimensions Ø 3×10 mm as a function of temperature (T) were registered. Obtained heating curves were used to precisely determine the critical temperatures (critical points) for the tested steels, while the differentiation of obtained cooling curves allowed to precisely define the temperatures of the beginning and the end of particular transition to draw CCT diagrams.Four CCT diagrams worked out for the tested hypoeutectoid steels (for quenching of steel) are -in the majority of steelsseparated by the undercooled austenitic range and are of the letter "C" shape. However, for steels with Mn and Ni the separation of diffusive transformations from the bainitic transformation by the stable austenitic range is not observed. Hardenability of four investigated hypoeutectoid steels is similar, but still not high. To obtain martensite in the microstructure of these steels, it is necessary to apply the cooling rate higher than 25• C/s. The exception constitutes the Mn -Ni steel, in which only cooling with the rate higher than 50• C/s allows to achieve the martensitic microstructure and to avoid diffusive transformations (pearlitic and ferritic).Keywords: microstructure, hypoeutectoid steel, CCT diagram, hardenability, alloying elements W artykule zamieszczono wyniki badań mikrostruktury, twardości stali podeutektoidalnych Mn-Cr-Ni imitujących składem chemicznym stale do ulepszania cieplnego. Celem badań jest analiza kinetyki przemian fazowych przechłodzonego austenitu stali różniących się zawartością pierwiastków stopowych w składzie chemicznym.Badania metalograficzne wykonano na mikroskopie świetlnym Axiovert 200 MAT. Zgłady wytrawiono 3% nitalem (3% roztwór HNO 3 w C 2 H 5 OH).Badania dylatometryczne wykonano przy użyciu dylatometru L78 R.I.T.A. Za pomocą dylatometru rejestrowano zmiany wydłużenia (∆l) próbek o wymiarach Ø 3×10 mm w funkcji temperatury (T). Otrzymane krzywe nagrzewania posłużyły do precyzyjnego wyznaczenia temperatur krytycznych (punktów przełomowych) dla badanych stali. Z kolei, otrzymane krzywe chłodzenia różniczkowano, co pozwoliło precyzyjnie określić temperatury początków i końców poszczególnych przemian dla wykonania wykresów CTPc.Opracowane cztery wykresy CTPc dla badanych stali podeutektoidalnych (do ulepszania cieplnego) są w większości rozdzielone zakresem trwałości przechłodzonego i mają kształt litery "C". Jednak dla stali z Mn i Ni nie...