Effect of Ferrite on the Precipitation of σ Phase in Cast Austenitic Stainless Steel Used for Primary Coolant Pipes of Nuclear Power Plants

Abstract

The effect of ferrite phase on the precipitation of σ phase in a Z3CN20.09M cast austenitic stainless steel (CASS) used for primary coolant pipes of pressurized water reactor (PWR) nuclear power plants was investigated by using isothermal heat-treatment, optical microscopy (OM), transmission electron microscopy (TEM) and electron probe microanalysis (EPMA) techniques. The influence of different morphologies and volume fractions of ferrite in the σ phase formation mechanism was discussed. The amount of σ phase precipitated in all specimens with different microstructures increased with increasing of aging time, however, the precipitation rate is significant different. The formation of σ phase in specimens with the coarsest ferrite and the dispersively smallest ferrite is slowest. The lowest level Cr content in ferrite and fewest α/γ interfaces in specimen are the main reasons for the slowest σ precipitation due to they are unfavorable for the kinetics and thermodynamics of phase transformation respectively. By contraries, the fastest formation of σ phase takes place in specimens with narrow and long ferrite due to the most α/γ interfaces and higher Cr content in ferrite which are beneficial for preferential nucleation and formation thermodynamics of σ phase.

Keywords:
Cast austenitic stainless steel; ferrite; σ phase; precipitation behavior; microstructure

1. Introduction

Cast austenitic stainless steels (CASS), which are characterized by the dual phase microstructure in which the island α-ferrite phase distributes in the γ-austenite matrix, possess excellent synthesis mechanical properties, good workability and high resistance to localized corrosion in chloride environments^1-4. Consequently, they are widely used in the primary coolant pipes of nuclear power plants and other engineering applications such as oil, chemical petrochemical, marine industries. However, several undesirable precipitated phases including α', M₂₃C₆, σ, χ, and π can form in these steels when they are exposed to the temperature region from 320°C to 950°C for a period of time^5-7. Generally, these secondary precipitates are harmful for properties of stainless steels.

Among all the precipitates mentioned above, σ phase is usually considered to be the most harmful. The presence of σ phase in stainless steels not only severely decreases the toughness of steels but also negatively impacts the corrosion resistance^7,8. However, recently it is reported that the precipitation of σ phase is beneficial for the creep strength and hot tensile strength of stainless steels although some researchers hold opposite views^9,10. Because of its significant influence, the precipitation of σ phase has been research by lots of workers. The results showed that the composition of alloys is the most important factor for σ precipitation^11-13. Ferritic stabilizer such as Cr, Mo and Si can promote the precipitation. In fact, the microstructure of stainless steels including grain size, α/γ interface ratio can affect the formation of σ phase too^11,14-16. Generally, σ directly formed in α/γ dual phase stainless steels by the eutectoid decomposition, α → σ + γ₂^17,18. So, ferrite phase may be one of important factors for the σ precipitation in stainless steels especially for CASS with a dual phase microstructure that less ferrite phases distribute in austenite matrix. Up to now, however, very few attempts have been made to investigate the effect of ferrite on the precipitation of σ phase in CASS. In this present work, the precipitation behavior of σ phase in a Z3CN20.09M CASS used for primary coolant pipe of nuclear power plants with different volume and morphology ferrite was investigated. Meanwhile, the mechanism of ferrite effect was elucidated.

2. Experimental Materials and Methods

The materials studied were cut from a Z3CN20.09M CASS primary coolant pipe of pressurized water reactor of nuclear power plants. The pipe was fabricated by electric-arc and argon-oxygen decarburization melting first, and then by moulded casting followed by air cooling and solution treatment (1180 °C, 8 h) followed by water quenching. The chemical composition of Z3CN20.09M CASS is C 0.024, Si 1.09, Mn 1.11, P 0.023, S 0.0039, Cr 20.16, Ni 9.06, Cu 0.031, Co 0.026, Nb+Ta 0.066, Mo 0.26, N 0.033, Ti 0.0027, Fe balance.

In order to illustrate the effect of ferrite on the precipitation of σ phase, Z3CN20.09M specimens with different microstructures were obtained by using different methods. Specimen A was annealed at 1350 °C for 20 h, specimen B was hot forged at 1180°C, specimen C was cut from the top of a part of primary coolant pipe and specimen D was cut from the bottom of a part of primary coolant pipe (Fig.1). All the as-received specimens were aged at 750 °C for different time to conveniently elucidate the precipitation behavior of σ phase in Z3CN20.09M CASS with different microstructure, because the higher kinetics of σ phase formation occurs at 750 °C¹⁹.

Figure 1
Specimen C and D of Z3CN20.09M CASS cut from the top and bottom of a part of primary coolant pipe.

Specimens were ground by using wet abrasive paper up to 2000^# and then polished using diamond paste to a finish of 1.5 µm, and finally rinsed in distilled water, ultrasonically cleaned and dried in air. Microstructures of specimens were revealed by electrolytic etching in a 20 wt% NaOH distilled water solution at room temperature with direct voltage 3 V for 10 s. Microstructures of the specimens were observed by CIKONG 4XCE optical microscopy (OM) after etching in the electrolyte. Volume fractions of precipitates, ferrite phase and the mean size of ferrite in the samples were obtained through the quantitative metallography analysis software (Image-Pro Plus 6.0) on 20 optical measurements for each specimen. The mean size of ferrite is denoted by mean length and width of ferrite phase. σ phase in this steel were detected by JEOL JEM-2010 transmission electron microscopy (TEM). The quantitative compositions of the austenite and ferrite phase in the specimens were measured by JEOL JXA-8100 electron probe microanalysis technique (EPMA).

3. Results and Discussion

3.1 Microstructure of as-received Z3CN20.09M CASS

Fig.2 shows the microstructure of A, B, C and D four Z3CN20.09M CASS specimens with different ferrite phase, revealing that only austenite (gray) and ferrite (dark) phases exist in the steel. Fig. 3 displays the ferrite contents and ferrite mean sizes in these four specimens A, B, C, D. The values are about 37, 12, 13, 8 volume% and 230, 96, 98, 18 µm respectively. From Fig. 3, one can also see that the α/γ phase boundary ratio in specimen A is the lowest level and that of specimen B is the highest. Moreover, morphology of ferrite in four specimens is also obviously different. The ferrite in specimen A is the coarsest and the ferrite in specimen D is the smallest, while, the typical long and narrow ferrite can be found in specimen B (Fig. 2b).

Figure 2
Microstructure of Z3CN20.09M specimens with different ferrite phase (a) annealed at 1350 °C, (b) hot forged, (c) containing 13% volume ferrite, (d) containing 8% volume ferrite, these specimens are named A, B, C, D respectively.

Figure 3
Four Z3CN20.09M primary coolant pipe specimens with different ferrite contents and sizes and austenite/ferrite phase boundaries.

By means of Thermo-Calc software, a phase diagram of the Z3CN20.09M CASS using chromium as a variable was computed, and the result is shown in Fig. 4. The composition of the Z3CN20.09M CASS is indicated by a broken vertical line (Fig. 4a). It can be seen that the primary δ-ferrite solidifies first and then the δ → γ transformation takes place. The nucleation and growth of the austenite phase is a diffusion-controlled process which is affected strongly by the degree of super-cooling²⁰. On rapid cooling, although the nucleation easily occurs in the ferrite phase, the growth of the austenite phase will be restrained due to insufficient time for the diffusion of alloy elements. Thus, the larger ferrite grains and also more ferrite remained in the structure of the Z3CN20.09M CASS pipe (Fig. 2c). By contrast, slow cooling (low cooling rate) would promote the diffusion of austenitic stabilized elements, such as Mn, N and Ni^21,22. Thus, more austenite formed from the ferrite phase, resulting in smaller ferrite phase in the inside of the pipe (Fig. 2d)^21,23. When Z3CN20.09M CASS annealed at high temperature, some austenite (γ) would be transformed to ferrite (δ) in order to satisfy the thermodynamics equilibrium of austenite and ferrite phase. During the process of γ → δ transformation, ferrite grains grown continuously by means of elements diffusion, so the volume fraction of ferrite increased and they become coarser. According to the phase diagram, on equilibrium state the ratio of γ/δ at 1350℃ is nearly 1:1. This accords with the high temperature annealing experimental result approximately (Fig. 2a).

Figure 4
Phase diagram of Z3CN20.09M computed using Thermo-Calc software (a) the composition of Z3CN20.09M is indicated by a dashed line, (b) phase fractions of ferrite, austenite, σ-phase and M₂₃C₆ as a function of temperature.

3.2 Precipitation of σ phase in Z3CN20.09M CASS with different microstructures

Fig. 5 shows the optical microstructure of Z3CN20.09M steel with different ferrite aged at 750 °C for 1, 24, 50 and 200 h. In these four aged specimens, precipitates can be found and their volume fraction increased with aging time. It is sure that the precipitates are almost all σ phases and a little M₂₃C₆ carbide at γ/α interface in terms of previous works¹⁹. Fig. 6 indicates the TEM micrograph of the Z3CN20.09M specimen aged at 750 °C for 200 h, detecting the σ phase with a tetragonal structure and secondary austenite (γ₂) with FCC structure. Although, the amount of σ phase in all specimens increased with the increase of aging time, the precipitation rate (or transformation ratio of α→σ) is significant different. Less σ phase precipitated in the aged specimens A with more and coarse ferrite than that in others at the same aging time. However, the most σ phase precipitated in the aged specimens B at the same aging time. Fig. 7 displays the transformation ratio of ferrite in different specimens. One can see that when aging for the same time, for example 24h, the transformation ratio of α→σ in aged specimen A is the minimum level and about 10%, while, the value in specimen B is the maximum and higher than 50%. This indicates the coarser the ferrite, the slower the formation of σ phase and the narrower or finer the ferrite, the faster the precipitation of σ phase. It is necessary to discuss the mechanism of microstructure effect on σ formation behavior for elucidating the phenomenon.

Figure 5
OM photographs of Z3CN20.09M specimens with different microstructure aged at 750°C for different times (a) specimen A, (b) specimen B, (c) specimen C, (s) specimen D.

Figure 6
TEM micrograph of the Z3CN20.09M specimen aged at 750 °C for 200 h.

Figure 7
Transformation ratio of α→σ in specimens with different microstructure aged at 750 °C for different time.

3.3 Mechanism of σ precipitation in Z3CN20.09M CASS dependent on microstructure

The precipitation behavior of σ phase in stainless steels depends on many factors including chemical compositions, heat-treatment process and microstructure, etc¹¹. Ferrite is very important for cast austenitic stainless steels and plays an important role in the properties of cast austenitic stainless steels. There is always higher Cr and Mo concentrations in ferrite phase since Cr, Mo are ferrite stabilized elements. Because Cr and Mo facilitate σ phase precipitation significantly, so ferrite is a beneficial site for the precipitation of the σ phase²⁴. It is well known that σ precipitates in duplex stainless steels by the eutectoid decomposition of α ferrite: α → σ + γ₂ and its nucleation and growth from ferrite to the α/α grain boundaries or α/γ interfaces strongly depends on Cr-diffusion²⁵. On one hand, there are the most high energy α/γ phase boundaries in specimen B (Fig.2, 3), which provide many preferential sites for σ nucleation. Furthermore, the diffusion of Cr in these interfaces is fast and beneficial for growth of σ phase. On the other hand, Cr content of ferrite in specimen B is much higher (about 26%, Fig. 8) and is close to the value of Cr in σ phase²⁶. Thermodynamically, this ferrite with more solid solution Cr is also more beneficial for σ phase formation. Compared with other specimens, there are not only the fewest α/γ interfaces but also the lowest Cr content of ferrite in specimen A. These are unfavorable for nucleation and growth of σ phase from both kinetics and thermodynamic aspects. Therefore, the formation of σ phase is the fastest in specimen B and the slowest in specimen A. Although there are almost the same Cr content of ferrite and phase boundaries in specimens C and D, the size and volume fraction of ferrite in specimen D is smaller and fewer than those in specimen C (Fig. 3, 5). Moreover, the ferrite phases in specimen D are also more dispersive (Fig. 3). As a result, the concentration of Cr, Mo elements in specimen D may be more uniform. It is relatively difficult to obtain Cr, Mo concentration fluctuation that is necessary for solid phase transformation. This is unfavorable for nucleation of σ phase. Whereas, the aggregated larger and more ferrite phases in specimen C not only provide more sites for σ phase formation, but also easily induce the concentration fluctuations of Cr, Mo elements. Those can promote σ phase precipitation. Thereby, the formation of σ phase in specimen C is faster than that in specimen D even if there is a similar thermodynamics for σ phase precipitation in specimens C and D because of the almost same Cr content in ferrite phase of the two specimens.

Figure 8
Cr content in Z3CN20.09M specimens with different ferrite

4. Conclusions

1. Although, the volume fraction of σ phase in all Z3CN20.09M CASS specimens with four ferrite phase specimens increased with aging time, there is markedly difference in the σ formation rate.

2. The precipitation of σ phase in specimens with the maximum and coarsest ferrite (specimen A) and with fewest and smallest dispersive ferrite (specimen D) is the lowest. By contraries, the formation of σ phase in specimen with narrow and long ferrite (specimen B) is the fastest. The faster formation, while, takes place in specimen with aggregated larger and more ferrite (specimen C).

3. The lowest level Cr content in ferrite and fewest α/γ interfaces in specimen are the reason for the slowest precipitation of σ phase due to they are unfavorable for the kinetics and thermodynamics of phase transformation respectively.

4. The dispersive small ferrite is favorable for Z3CN20.09M CASS owing to that restrains the σ phase precipitation.

5. Acknowledgements

This work was financially supported by the National Natural Science Foundation of China [grant number 51501001] and Anhui Provincial Natural Science Foundation [grant number 1508085QE102].

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Publication Dates

• Publication in this collection
  28 Sept 2017
• Date of issue
  Nov-Dec 2017

History

• Received
  21 Feb 2017
• Reviewed
  10 Aug 2017
• Accepted
  24 Aug 2017