Recrystallization-based formation of uniform fine-grained austenite structure before polymorphic transition in high-strength steels for Arctic applications

Abstract

Background

Growing demand for materials suitable for Arctic marine constructions necessitates the development of lowcost steels with excellent low-temperature properties. One way of addressing this issue is to obtain a finegrained structure by careful control of the recrystallization process.

Methods

The research methods used in this paper includes conducting experiments and making observations. The study investigates mechanisms of grain structure formation in low-carbon cold-resistant F620 steels additionally alloyed with Nb or V during hot plastic deformation.

Results

The obtained results evidence that static recrystallization is the most effective means to refine the austenite structure under conditions of industrial rolling. On this basis, a temperature-strain scheme of fractional hot rolling is proposed that provides the most refined uniform structures of bainite and/or martensite after quenching. Additionally, the results show that substitution of the alloying element V by Nb makes the structure of the hot-rolled austenite more finely dispersed.

Conclusions

New cold-resistant F620 steels for Arctic applications alloyed with Nb of 50-mm thickness were produced utilizing the research results. These grades of steels have reduced alloying content and exhibit improved properties, in particular, cold resistance down to −60 °С and high fracture toughness at −50 °С.

Background

Simultaneously high levels of strength and cold resistance are commonly obtained in shipbuilding steels by alloying with elements such as Ni, Mo, Cr, Cu, Nb, Ti, and V which add considerably to the cost of the steel (Khlusova et al. 2007). Consequently, the growing demand for Arctic steels is promoting research in and development of suitable low-cost steels and their respective technologies. At the same time, however, quality requirements are becoming still more severe. For example, the Russian Maritime Register of Shipping has imposed more stringent requirements on ductility, cold resistance, and fracture toughness of “Arc-steels” while maintaining previous high-strength requirements (Russian Maritime Register of Shipping. Rules for the Classification & Construction and Equipment of Mobile Offshore Platforms 2012). Such a complex combination of qualities is feasible in thick rolled products only when fine-grained structures are present (Calcagnotto et al. 2009; Leinonen 2004; Salvatori 2006). Refining of austenite grains is possible by utilizing recrystallization (dynamic—DRx, metadynamic—MDRx, and static—SRx) (Gorelik et al. 2005) and fragmentation (Kodzhaspirov et al. 2006) processes under specific thermo-mechanical conditions (Fernández et al. 2003). In addition, the structure formation over the whole cycle of hot rolling is sensitive to small additions (~0.01 %) of Nb, Ti, or V, which hinder boundary migration and, hence, grain growth (Sha & Sun 2009; Sha et al. 2011; Jung et al. 2011). The present paper investigates the effects of temperature and strain degree on DRx and SRx kinetics in austenite of cold-resistant high-strength steel F620 presented with two micro-alloying options—with V or Nb. The chemical composition of steel F620 according to various certification societies and the one used in this study is provided in Table 1.

Table 1 Chemical composition of F620, wt. %

Methods

Dynamic recrystallization experiments

The threshold strain (εр) related to DRx start was determined with stress-strain diagrams (σ-ε) based on characteristic stress maxima. Stress-strain diagrams for the steels in this study are shown in Fig. 1. At the highest temperature, 1150 °С, both steels display maximum stress values (σ ≈ 90 MPa) at lower values of strain (εp ≈ 0.3 %), as shown in Fig. 1 a by the red dotted line. Here, Nb augments εp by about 0.005 %, slightly hindering DRx though not stopping the process. When the temperature decreases down to 1050 °С, the Nb effect becomes most pronounced, since, unlike steel F620 alloyed with V (εp ≈ 0.45 %), there are no signs of austenite DRx in F620 alloyed with Nb up to true strain of 0.9 %. At the lowest temperature, 950 °С, the DRx process ceases in both steels. The diagrams in Fig. 1 also show that the general hardening effect due to Nb becomes stronger when the deformation temperature is reduced.

Fig. 1

Loading stress-strain diagrams of F620 with V and Nb steels at а Т = 1150 °С, b Т = 1050 °С, and c Т = 950 °С

In order to form a sufficiently uniform refined structure, the small austenite grains inherent in DRx should cover a high enough volume fraction. However, even at T > 1050 °C, this is possible only if single strains exceed 0.9 %, which is unrealistic in industrial rolling. Therefore, austenite formation during DRx remains incomplete, and hence, an unwanted non-uniform structure forms (coexistence of fine and coarse grains) that reduces the ductility of the steel. As evident in Fig. 1, this characteristic previously known with the traditional steel F620 alloyed with V (Zisman et al. 2012) remains valid for its modification alloyed with Nb. Therefore, the growth of threshold εp due to Nb proves to have an additional positive effect because it more reliably excludes incomplete DRx and related grain size variation. The grain size was measured according to ISO 643: 2003 standard.

Static recrystallization experiments

To investigate SRx of austenite, the stress relaxation method (Zisman et al. 2012; Perttula & Karjalainen 1998) was implemented on a Gleeble 3800 simulator. The selected degrees of 0.25 and 0.10 of single strains correspond, respectively, to the maximum thickness reduction during rough rolling and the average reduction in finish rolling of the investigated steels. Distinct changes in the softening rate dσ/dt allow determination of the incubation period of SRx and the time span of its primary stage (Zisman et al. 2012; Perttula & Karjalainen 1998). Stress relaxation curves for austenite of F620 alloyed with V and Nb, correspondingly, are indicated in Figs. 2 and 3 by labels “V” and “Nb.” When the incubation period and duration of primary SRx could be derived from the diagrams, these time parameters are indicated by light and dark circles, respectively; stars indicate the time when the SRx degree reached 80 %. Following, the SRx degree is evaluated as (Zisman et al. 2012)

Fig. 2

Stress relaxation of F620 steel alloyed with V and Nb after true strain of 0.25 % at temperatures of а 1000 °С, b 950 °С, c 900 °С, and d 850 °С

Fig. 3

Stress relaxation of F620 steel alloyed with V and Nb after true strain of 0.10 % at temperatures of а 1100 and 1150 °С, b 1000 °С, c 950 °С, and d 900 °С

$$ P(t)=\left(\upsigma \max -\upsigma \mathrm{t}\right)/\left(\upsigma \max -\upsigma \min \right), $$

(1)

where σmax and σmin are the maximum and minimum stress magnitudes during the SRx, respectively, and σt is the stress magnitude at a current time t.

Stress relaxation diagrams after ε = 0.25 % (Fig. 2) show that during technological pauses (several seconds or tens of seconds) austenite SRx in both steels becomes complete only at Т ≥ 1000 °С. At T = 950 °С, this process remains uncompleted in the steel micro-alloyed by Nb and at lower temperatures in both steels. After ε = 0.10 % (Fig. 3), SRx becomes much slower and becomes complete in the abovementioned pauses only at relatively high temperatures of Т ≥ 1100 °С. Earlier termination of SRx due to Nb addition accelerates the growth of the dislocation density and hence extends the range of austenite fragmentation (subgrain structure evolution) to higher temperatures (Kodzhaspirov et al. 2006; Rybin 1986). Nevertheless, previous SRx still remains significant, since the fragmentation rate increases with the grains’ refinement (Rybin 1986).

Results and discussion

Samples of both F620 steels alloyed with V or Nb were subjected to two treatments on the Gleeble 3800 simulator. The treatments included five sequential strains, separated by pauses, in a temperature range of 950 to 1150 °С. In the first treatment, the pauses were not regulated; in the second treatment, the pause durations, increasing with the temperature reduction, were selected to provide complete primary SRx in each case. The true strains, strain rate, and following cooling rate were 0.15 %, 1 s⁻¹ and 30 °С/s, respectively.

As can be seen from Figs. 4a–c and 5а–c, the most dispersed structure and therefore the highest hardness (Figs. 4d and 5d) are provided by the treatment with regulated pauses selected based on the austenite SRx kinetics of F620 steels alloyed with V or Nb.

Fig. 4

Microstructure F620 steel alloyed with V: а transformed from austenite exposed for 60 s at Т = 1200 °С, D _γ  = 120 μm; b austenite deformed with pauses regulated, D _γ  = 17 μm; c not regulated, D _γ  = 90 μm; and d microhardness

Fig. 5

Microstructure of F620 steel alloyed with Nb: а transformed from austenite exposed for 60 s at Т = 1200 °С, D _γ  = 100 μm; b austenite deformed with pauses regulated, D _γ  = 15 μm; c not regulated, D _γ  = 50 μm; and d microhardness

Rolled products of up to 50-mm thickness were fabricated from a new lower-alloyed cold-resistant steel, F620 (alloyed with Nb), with a rolling scheme based on the above findings. The average tensile strength was 760 МPа (700–890 МPа required by specification) and the yield stress 700 МPа (≥620 МPа required by specification). The alloying level, as reflected by the toughness parameter Рcm, was 0.22 %. Apart from the required strength, the rolled products of Arc-steel showed high ductility (δ ₅ ≥ 20 %), good toughness, and cold resistance down to −60 °С (Figs. 5 and 6). All tests were performed on whole thickness samples. The requirements for steels are provided according to Russian Maritime Register of Shipping (RMRS) rules. The quality characteristics of the lower-alloyed cold-resistant steel are the result of the finely dispersed structures of bainite-martensite mixture obtained by γ-α transition from the fine-grained austenite. The testing results of F620 steels alloyed with V or Nb demonstrate the effectiveness of the new procedure.

Fig. 6

Properties of F620 steel. а Parameters of cold resistance (characteristic temperatures Ткб and NDT); b fracture toughness (CTOD at −40 °С)

Conclusions

The outcomes and conclusions of the conducted research are:

• 1. During rough rolling (Т > 1050 °С for F620 steel alloyed with V and Т > 1100 °С for Nb-alloyed steel), incomplete DRx can occur, resulting in non-uniformity (grain size) of the austenite structure. To prevent this unwanted effect, it is necessary to regulate successive deformations.

• 2. A uniform fine-grained austenite structure may be obtained during rough rolling if primary SRx is completed within each pause; to this end, it is necessary to gradually increase the durations of the pause between successive deformations in the range 1150–950 °С for F620 V-alloyed steel and 1150–1050 °С for F620 Nb-alloyed steel.

• 3. Substitution of V by Nb in Cr-Ni-Mo steels makes the structure of the hot-rolled austenite more finely dispersed as a result of a number of effects: (а) limitation on grain growth during the metal heating before rolling; (b) prevention of DRx, which may be only partial (incomplete) for technological reasons and can result in structural non-uniformity; (c) prevention of growth of new grains formed by primary SRx; and (d) extension to higher temperatures of the range of austenite fragmentation, forming new interfaces within grains.

• 4. Rolled products of 50-mm thickness fabricated from a new cold-resistant Nb-alloyed F620 steel with reduced alloying and made following the discussed procedure display improved product characteristics, in particular, cold-resistance down to −60 °С and high fracture toughness at −50 °С. The steel is recommended for Arctic applications.