VERIFICATION OF DEFORMATION BEHAVIOUR OF BULK TRIP STEEL

Nov 19th – 21st 2014, Pilsen, Czech Republic, EU

VERIFICATION OF DEFORMATION BEHAVIOUR OF BULK TRIP STEEL Jozef ZRNIK1, Ondrej MURANSKY2, Zbyšek NOVY1, Peter SLAMA1 1COMTES 2Institute

FHT Inc., Prumyslova 995, 33441 Dobrany, Czech Republic, [email protected]

of Materials Engineering, ANSTO, Menai NSW 2234, Australia, ondrej.muransky@ hot.mail.com

Abstract Experimental verification of various thermo-mechanical (TM] processing schedules, with aim to modify the structure characteristics using press forging of Si-Mn TRIP (Transformation Induced Plasticity) steel, was carried out. High strength and ductility of TRIP steels is attributed to the TRIP effect resulting from the strain induced martensitic transformation of the retained austenite in the multiphase (ferrite, bainite, martensite) microstructure. In order to rationalize the retained austenite (RA) volume fraction in steel microstructure, several TM schedules were emplozed at experiment where different austenite conditioning was considered. The various multiphase structure characteristics were then resulting after TM processing of steel, where different volume fractions of ferrite, bainite and RA were received in the steel. The modification of structural characteristics of steel then influenced the deformation behaviour and mechanical properties TRIP steel. The present work also focused on monitoring of RA transformation during incremental mechanical straining using in-situ neutron diffraction technique. This non-convenient experimental method was used to characterize the kinetics of RA transformation and its stability during consecutive straining.

Keywords: TRIP steel, austenite conditioning, phase transformations, structure, properties, austenite stability. 1. INTRODUCTION The improvement of steel strength without deteriorating their formability remains one of the most challenging goals for material engineers. Low alloyed TRIP-assisted steels belong to the group of high strength steels with multiphase structure offering such attractive combination of strength and ductility. The microstructure of TRIP steels consists of ferrite, bainite and retained austenite [1, 2]. An extraordinary combination of high strength and ductility at forming results from the interaction of individual constituent of microstructure. It is known that the high ductility arises mainly from the processes related to the strain induced martensitic transformation of the metastable retained austenite during the straining [2, 3]. The purpose of this study is to contribute to a better understanding of the factors governing plastic straining in multiphase microstructure of TRIP steels. It is believed that not just sufficient volume fraction of the retained austenite is necessary to achieve convenient conditions for TRIP effect in low alloyed steels. But also other structure characteristics, such as morphology, size of the austenite islands and their distribution, solute enrichment and mechanical stability have to be considered in the process of the TRIP steel development as well. For this scope we have been studying TRIP steels contain rather same volume fraction of retained austenite but after different thermomechanical processing. 2. EXPERIMENTAL PROCEDURE The low alloyed Si-Mn steel, the chemical composition of C 0.19, Mn 1.45, Si 1.9, P 0,02, Cr 0,07, Ni 0,02, Cu 0,04, Al 0,02, Nb 0,003, was used for various thermomechanical processing (TM). The three bulk samples of experimental TRIP steel in form of bars. of 25 mm in diameter and 70 mm in length, were then subjected to various TM treatments applying various thermal and deformation conditions, Fig.1. The steel


samples in form of bars of 25 mm in diameter and 70 mm in length were subjected to the three different thermomechanical procedures in order to obtain a different TRIP steels structures providing then various and different mechanical properties as regards a relation of strength and ductility. The following design procedures in details have been designed: Specimens A,B: 1) heating to T=1000°C/30min. → 2) first compression ε1 → 3) cooling to: A  T1, B  T1 → 4) second compression ε2 → 5) first transformation γ-α at T= 750°C/300sec. 6) water quenching → 7) second transformation at 420°C/300s → 8) air cooling (Fig.1)

Fig. 1. Scheme of special TM treatment of steel.

Specimens C: 1) heating to T=850°C/35min. → 2) cooling to T1 → 3) compression ε1→ 4) first transformation γ-α at T= 750°C/300sec. → 5) water quenching → 6) second transformation at 420°C/300s →7) air cooling. The Ac1 and Ac3 temperatures, as well as, the required critical cooling rates were estimated from the continuous cooling transformation (CCT) diagram for the initial low alloyed steel [4,5]. The specimens (A,B,C) for tensile test of 6x2 mm in the cross-section were manufactured from the bulk TRIP specimens steels that had been treated according to above mentioned (A,B,C) thermomechanical schedule conditions. In-situ neutron diffraction experiments during the tensile tests were carried out at TKSN-400 diffractometer in NPI Rez, Czech Republic. The diffractometer operates at instrumental resolution of Δd/dhkl=2x10-3. However, since such a high instrumental resolution is achieved only in a relatively narrow 2θ-band (of about (2θ) ≈ 7˚), one or two diffraction line profiles can be investigated at the same time. In the present experiment, the detector window was set to cover both ferrite (110) and austenitic (111) reflections, simultaneously. The tensile tests were performed at room temperature and neutron diffraction spectra were recorded during temporary stops of the deformation machine. The holding time of 1 hour in each step was necessary to achieve sufficiently good statistics in measured spectra. 3.

RESULTS AND DISCUSSION 1000

Stress / MPa

800

600

400

200

TRIP sample A TRIP sample B TRIP sample C

0 0

2

4

6

8

10 12 14 16 18 20 22 24 26 28

Strain / %

Fig.2 Stress-straincurves curves three TRIP steels FFig. 2. Stress-strain of of thethe three TRIP steels.

Three TRIP steel specimens (A,B,C) with rather different volume fraction of the retained austenite (15- 20 %), were examined in-situ upon tensile loading at room temperature. From stress-strain curves in Fig.2 is clearly seen that each of the TRIP samples have exhibited the different mechanical properties. The visible differences were achieved in yield strengths. The sample A has the highest yield strength and elongation, whereas the sample C has the smallest yield strength, but on the other hand the highest tensile strength. Mechanical properties of TRIP steel strongly depend on the composition of microstructure, however in our case the volume fraction of

present phases in structure was rather similar. There are a few other influences which can affect the behaviour of TRIP steel during the deformation. Characteristics such as a phase morphology, distribution,


grain size and carbon content in retained austenite are very important for the transformation kinetics of the retained austenite, which as it is known, has the biggest effect on the exhibited mechanical properties of this type of steels [5, 6].

of Austenite / %

100


50

Volume fraction

Volume fraction

100

75

(!)

75

(!)

of Austenite / %

The evolution of the austenite transformation during the straining of specimens manufactured by different thermomechanical treatments is shown in Fig. 3 and Fig. 4. The changes in the integral intensity of the austenite reflection (111) during the tensile test can be considered as the change in the volume fraction [6]. The volume fraction of the retained austenite at the beginning of tensile test was taken as 100%, just for description of the transformation kinetics. This single peak method analysis can be use as a good approximation for describing kinetics of austenite transformation during the straining [7].

25

0

0

2

4

6

8

10

12

14

16

18

20

22

24

Strain / %

Fig. 3. Evolution of the austenite volume fraction in dependence on applied stress during the tensile test.

50


25

0

0

200

400

600

800

1000

Stress / MPa

Fig. 4. Evolution of the austenite volume fraction in dependence on applied strain during the tensile test,

As evidenced by the NPI data (Fig.3, Fig.4) taken in axial arrangement, the transformation proceeds in slightly different ways for each of tested specimens. From the figures is obvious that the transformation starts the most massively in the sample C, at strain of ε≥0.005 (400MPa) and at strain of ε≥0.12 ( 890MPa) almost all of present retained austenite is transformed to the martensite. Whereas, the transformation in other two samples starts at higher levels of strain (stress), what is related with higher level of yield strengths of the present constituents (Fig.2, Tab.1). From the deformation records for sample A it can be seen, that this sample exhibits the highest elongation. The martensitic transformation of retained austenite continued even at the highest strains of ε≥ 0.18. In all TRIP specimens at the end of tensile test (failure of samples) in the microstructure still could be found some untransformed stabilized austenite. This austenite does not contribute to the steel deformation, what is then expressed in the total ductility of the specimen, (Fig.2) . It is then supposed that the untransformed retained austenite is present in microstructure in Tab.1. Elastoplastic properties of phases in TRIP steel. the form of the laths inside the bainite islands [8]. In consequence of that is Sample A Sample B Sample C highly saturated by carbon, which has the E σ0 E σ0 E σ0 biggest influence on the stability of the GPa MPa GPa MPa GPa MPa retained of the retained present there. α-matrix 193 607 206 452 206 350 Additionally,the elastic lattice strain of the γ-retained 229 942 220 694 190 690 phases present in the microstructure has been measured as a function of macroscopic strain imposed to the specimens during the in-situ tensile test. This measurement allows determining the stress partitioning between the phases during sample straining.


Indeed, the elastic lattice strains are converted into stresses thanks to the knowledge of the elastic constants of the diffracting phases [9]. Fig.5 and Fig.6 present the macroscopic stress vs. lattice strain curves for the (110)α and (111)γ planes measured at all samples, respectively. At first, from the figures can be seen that the stress level is higher in the austenite than in the ferrite phase. All curves at the beginning show a linear evolution of the macroscopic stress with increasing lattice strains. The slopes correspond to the Young’s modulus for the specific crystallographic planes. The first change of the linear evolution corresponds to the yield strength of each phase [9]. 1000

1000

800 Stress / MPa

Stress / MPa

800


600

400

200

110

A) EF = 193.496 GPa (0 - 400 MPa)

600

400

200

0

C) EF = 205.796 GPa (0 - 400 MPa)

0.0000 0.0008 0.0016 0.0024 0.0032 0.0040 0.0048

Lattice strain Fig. 5. Measurement of the yield strength of α-matrix (ferrite, bainite) in dependence on applied stress during the tensile test.

111

= 228.682 GPa (0 - 400 MPa)

111

= 219.529 GPa (0 - 400 MPa)

111

= 190.038 GPa (0 - 440 MPa)

A) EA

B) EA

110

B) EF = 205.623 GPa (0 - 400 MPa) 110


0

C) EA

0.0000 0.0008 0.0016 0.0024 0.0032 0.0040 0.0048

Lattice strain Fig. 6. Austenite volume fraction evolution in dependence on applied stress during tensile test.

From the results shown in Tab.2, it is obvious than in all specimens the austenite is harder than ferrite (α-matrix), however in general the austenite is considered as a softer phase. But the unusual high carbon saturation of the austenite present in TRIP multiphase steels can be invoked as a cause of increase of its hardness [9]. Some authors as Irvine et all. showed that the effect of the carbon content on the yield strength of austenite is quite large [10]. CONCLUSIONS Results of in-situ neutron diffraction experiments focused on of monitoring phase evolution and on determining the stress partitioning between the phases, present in TRIP steels subjected to tensile loading at room temperature were reported. Valuable information on the kinetics of the austenite to martensite transformation during mechanical loading can be obtained by monitoring integral intensity of austenite reflection recorded in neutron diffraction experiments. In addition, in-situ neutron diffraction experiments also allowed characterizing the elastoplastic properties of the phases present in TRIP multiphase steels. These properties have strong influence on the transformation behaviour of the retained austenite during the straining and also critical effect on general mechanical properties of TRIP steel. As is seen from the results, the elastoplastic properties of the present phases can be markedly affected by choice of thermomechanical processing parameters. According to that not only volume fraction of retained austenite has the influence on mechanical properties of TRIP steels, but also the conditions (size, distribution, carbon saturation, morphology) of retained austenite and the state of surrounding (α-matrix) plays important role in affecting deformation mechanisms.


ACKNOWLEDGEMENT This work was supported by Grant Agency of the Academy of Science of the Czech republic (contract A1048107) and Grant Agency of Slovak Republic (contract MS 1/3218.The authors are grateful to the Grant Agency of the Academy of Sciences of the Czech Republic . LITERATURE [1]

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[2]

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[3]

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ZHAO, L., MORENO J., KURUIJVER, S.. SIETSMA, J., van der ZWAAG, S. TRIP-Aided Ferrous Alloys, Int. Con. on TRIP-Aided High Strength Ferrous Alloys, Ghent, Belgium, 2002, p. 141

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[8]

KWANG, K. P., et al.: Material Science Forum Vols. 408-412 (2002) pp. 571-576

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FURMÉMONT, Q. et al. Fundamental Materials Science of the TRIP Phenomenon, Int. Conf. On TRIP-Aided High Strength Ferrous Alloys, Ghent, Belgium, 2002, p. 39.

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IRVINE, K.J., LEWELLYN, D.T., PICKERING, F.B. JSII, 199, 1996 p. 153

….


The acknowledgements, please, write size 10 pt. in italics, bold and center it.

ŠABLONA PRO PŘÍPRAVU PLNÉHO TEXTU PŘEDNÁŠKY/POSTERU Doporučené členění příspěvku: Abstrakt (anglicky) Klíčová slova (anglicky) Úvod Hlavní text (obsahující zejména metodická východiska, experimentální část a výsledky a jejich diskusi) Závěr Poděkování Seznam citované literatury

Textový editor: písmo: řádkování: okraje:

MS WORD verze 97 a novější velikost 10 b., Arial 1,2 okraje stránky 20 mm ze všech stran

VERIFICATION OF DEFORMATION BEHAVIOUR OF BULK TRIP STEELNÁZEV ČLÁNKU (11 b., tučně, vycentrovat, mezery 12 před a 6 za, řádkování 1,2) Autoři (Jozef ZRNÍK1, Ondrej MURÁNSKY2, Zbyšek NOVÝ1 Jméno PŘÍJMENÍ) (11 b., vycentrovat, mezery 12 a 12, řádkování 1,2) COMTES FHT Inc., Dobrany,Průmyslova 995, Czech Republic, [email protected] Název a adresa instituce, e-mailová adresa (10 b., kurzíva, vycentrovat, mezery 6 a 0, řádkování 1,2) 2Institute

of Materials Engineering, ANSTO, Menai NSV 2234, AustraliaNázev a adresa instituce, e-mailová adresa (10 b., kurzíva, vycentrovat, mezery 6 a 0, řádkování 1,2)

Název a adresa instituce, e-mailová adresa (10 b., kurzíva, vycentrovat, mezery 6 a 0, řádkování 1,2)

Abstrakt (název 10 b. tučně, mezery 24 a 0) Abstrakt (text 10 b., mezery 3 a 0) by měly mít rozsah do 250 slov. Klíčová slova: (název 10 b. tučně, mezery 6 a 0) Počet klíčových slov (text 10 b., mezery 3 a 0) by měl být maximálně 5 1.

NADPISY KAPITOL (10 b., tučně, mezery 18 a 0)

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1.1

Název podkapitoly (10 b., tučně, mezery 12 a 0)

Q n 2. OBRÁZKY, ROVNICE, TABULKY  sinh   p   RT  Doporučujeme umístit obrázky a tabulky v rámci textu. Název tabulky

  A exp 

(Tab. 1) napište nad tabulku (10 b. tučně) a název obrázku (Obr. 1) napište pod daný obrázek (10 b.tučně). Samotný popis obrázku či tabulky je 10 b. S ohledem na elektronickou formu sborníku je možno do textu zařadit i barevné obrázky a grafy. Obrázky by měly být originální, nebo kvalitně naskenované. Málo výrazné fotokopie nebudou přijaty. Obrázky a grafy musí být součástí souboru referátu. Při nejasnostech je možno se s dotazy obrátit na sekretariát konference Rovnice napište do samostatného řádku vlevo s číslováním na konci řádku např.: (1)

PODĚKOVÁNÍ Poděkování pište velikostí písma 10 b. kurzívou, tučně a vycentrujte. LITERATURA Čísla odkazů na citovanou literaturu pište v hranatých závorkách bezprostředně za textem a v pořadí v jakém se vyskytují v textu. Nezačínejte na nové stránce, není-li to naprosto nezbytné. Odkazy na literaturu označte arabskými číslicemi v hranaté závorce průběžně, jak se vyskytovaly v textu, Velikost písma v literatuře je 9 b., zarovnání vpravo [1]

NOVÁK, J. Dějiny technického pokroku. 1. vyd. Praha: Akademia, 1998. 330 s.

[2]

NOVOTNÝ, K. Vliv teploty na deformační chování mosazných slitin. In Sborník z konference Tvařitelnost kovů. Ostrava: TANGER, 1997, s. 9-14.

[3]

KOVÁČ, J., KUPKA, A. Vliv křemíku na magnetické vlastnosti plechu. Hutnické listy, 1998, roč. 49, č. 11, s. 1216.

[4]

POLÁŠEK, Karel. Křivka napětí a deformace. In Metal 2000: 9. mez. metal. konference: 16. - 18. 5. 2000. Ostrava, Hotel Atom/Hotel Harmony, Česká republika [CD-ROM]. Ostrava: TANGER: Květen, 2000, s. 82-89. ISBN 80-85988-48-8.

VERIFICATION OF DEFORMATION BEHAVIOUR OF BULK TRIP STEEL

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