The hot ductility of Transformation Induced Plasticity (TRIP) and Twinning Induced Plasticity (TWIP) steels is reviewed, concentrating on the likelihood of cracking occurring on continuous casting during the straightening operation. In this review, the influence of high levels of Al, Si, P, Mn and C on their hot ductility will be discussed as well as the important role B can play in improving their hot ductility. Of these elements, Al has the worst influence on ductility but a high Al addition is often needed in both TWIP and TRIP steels. AlN precipitates are formed often as thin coatings covering the austenite grain surfaces favouring intergranular failure and making them difficult to continuous cast without cracks forming. Furthermore, with TWIP steels the un-recrystallised austenite, which is the state the austenite is when straightening, suffers from excessive grain boundary sliding, so that the ductility often decreases with increasing temperature, resulting in the RA value being below that needed to avoid cracking on straightening. Fortunately, the addition of B can often be used to remedy the deleterious influence of AlN. The influence of precipitation hardeners (Nb, V and Ti based) in strengthening the room temperature yield strength of these TWIP steels and their influence on hot ductility is also discussed.

High Al, twinning induced plasticity (TWIP) steels have high tensile strengths and excellent ductility but low yield strengths compared to other advanced high strength steels and this has limited their application. A.Vanadium addition is a possible answer but cracking on casting is a worry. Hot tensile tests were therefore performed on 1.5% Al, TWIP steels with vanadium levels approximately 0.05–0.7% (all wt-%). Only the 0.05% vanadium steel gave acceptable hot ductility but the room temperature yield strength was too low. In contrast, the Ti–B high 0.5% V steel which was as well as able to give a high yield strength due to precipitation hardening by vanadium carbide gave better ductility by boron segregating to the boundaries and strengthening them.

The dendritic AlN associated with poor ductility on straightening during continuous casting is believed to always crystallise out in the hcp structure. The present paper shows that AlN precipitation can also be present as an fcc phase. Because AlN precipitation is sluggish and needs suitable nucleants like MnS to aid its precipitation, the crystal structure of AlN is dependent on the order in which the austenite and MnS precipitate out during solidification. When austenite forms first, as with the 1Al transformation induced plasticity (TRIP) steel, MnS nucleants are not available and AlN is forced to precipitate at the austenite grain boundaries as fcc so encouraging intergranular failure. With the 1.5Al TRIP steel, on solidification, MnS is present in abundance, giving rise to the conventional hcp AlN.

The hot ductility of B-Ti-Nb-high Al (1.5%Al) containing TWIP steels having Ti/N ratios mainly in excess of 3.4/1 was obtained. After soaking at 1250°C, the tensile specimens were cooled at 12 or 60°C min⁻¹ to the test temperature and then strained to failure at 3 × 10⁻³ s⁻¹. Ductility was always good (reduction of area >40%), independent of Ti/N ratio or cooling rate. The good ductility is due to B segregation strengthening the grain boundaries and the low S level (0.005%S) limiting the volume fraction of MnS inclusions and restricting AlN precipitation to the matrix. Increasing the cooling rate, higher N levels and Nb resulted in a small improvement in ductility. An addition of V to the Nb-containing steels caused a slight deterioration in the hot ductility.

Cu-containing steels can suffer from hot shortness unless Ni is added to protect them but whether this problem also influences the straightening operation is not clear. Previous work on hot ductility has found that only when the tensile samples from Cu-containing steels are oxidised can any deleterious influence of copper be found. However, this paper shows that oxidation is not essential. It is more complex than that and, as Cu has been suggested for TRIP steels at levels up to 2.5% Cu to increase their strength and ductility, a greater understanding is required, both of hot shortness and cracking during straightening. The present paper explores the hot ductility behaviour of steels alloyed with Cu and Ni in the straightening temperature range, 700–1000 °C, when tested in air and in an argon atmosphere. Segregation of Cu to the sulphides and grain boundaries occurred allowing the formation of fine Cu₂S particles at the austenite grain boundaries favouring intergranular failure and this was more pronounced under oxidising conditions and required strain. It was concluded that a Cu addition, as well as causing hot shortness at higher temperatures will also cause cracking problems in the straightening temperature range in the more sensitive to cracking grades of steel and although the problems are different they are nevertheless interrelated and provided there is sufficient Ni, both may be avoided.

In this paper, the influence of small additions of Cr, Mo, Cu, Ni, B, Ca, Zr, and Ce on the hot ductility of advanced high-strength steels (AHSS) has been reviewed. Most of these small additions have a positive effect in improving hot ductility on straightening during continuous casting operations and should be considered when problems with cracking in continuous casting are encountered. In many of these cases, the reason for these generally small but important improvements in hot ductility is not known with certainty, but the segregation of these elements to the austenite grain boundaries, strengthening the bonding, is often suggested.