Abstract
This review paper concerns the development of the chemical compositions and controlled processes of rolling and cooling steels to increase their mechanical properties and reduce weight and production costs. The paper analyzes the basic differences among high-strength steel (HSS), advanced high-strength steel (AHSS) and ultra-high-strength steel (UHSS) depending on differences in their final microstructural components, chemical composition, alloying elements and strengthening contributions to determine strength and mechanical properties. HSS is characterized by a final single-phase structure with reduced perlite content, while AHSS has a final structure of two-phase to multiphase. UHSS is characterized by a single-phase or multiphase structure. The yield strength of the steels have the following value intervals: HSS, 180–550 MPa; AHSS, 260–900 MPa; UHSS, 600–960 MPa. In addition to strength properties, the ductility of these steel grades is also an important parameter. AHSS steel has the best ductility, followed by HSS and UHSS. Within the HSS steel group, high-strength low-alloy (HSLA) steel represents a special subgroup characterized by the use of microalloying elements for special strength and plastic properties. An important parameter determining the strength properties of these steels is the grain-size diameter of the final structure, which depends on the processing conditions of the previous austenitic structure. The influence of reheating temperatures (TReh) and the holding time at the reheating temperature (tReh) of C–Mn–Nb–V HSLA steel was investigated in detail. Mathematical equations describing changes in the diameter of austenite grain size (dγ), depending on reheating temperature and holding time, were derived by the authors. The coordinates of the point where normal grain growth turned abnormal was determined. These coordinates for testing steel are the reheating conditions TReh = 1060 °C, tReh = 1800 s at the diameter of austenite grain size dγ = 100 μm.
Highlights
The development of microalloying high-strength steel (HSS) to create high-strength, low-alloy steel (HSLA) began after World War II when market requirements were defined by the price of the steel plates and strips used in shipbuilding, oil-and-gas transportation and other industries
Physical-Metallurgical Substance of Grain Growth Depending on Reheating Conditions
Calculation of the dissolution temperature of precipitates as a function of thermodynamic constants and chemical composition is described by the following formula:
Summary
The development of microalloying high-strength steel (HSS) to create high-strength, low-alloy steel (HSLA) began after World War II when market requirements were defined by the price of the steel plates and strips used in shipbuilding, oil-and-gas transportation and other industries. The last pass was carried out nearly above the Ar3 line [1] This technology is often called thermomechanical treatment (TMT), sometimes as rolling at a controlled temperature [2], but both terms have been replaced by controlled rolling (CR). CR is characterized by the fact that the last passes are carried out at low-finishing rolling temperatures, which results in lower production costs by removing normalization annealing and increases mechanical properties and toughness through reducing the thickness of the rolled plates and strips. The advantage obtained by controlling the austenite structure is the formation of strongly deformed pancake grains from CR. These have to be maintained by rapidly cooling the deformed austenite immediately after the last rolling pass in order to provide a controlled phase transformation to the ferrite. Rapid cooling has to prevent the growth of ferrite grains and achieve a fine-grained final structure [3]
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