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Dr. Dmitri Kopeliovich
Large steel ingots are required for manufacturing electric power plant turbine shafts, generator rotor shafts, nuclear pressure vessels, chemical pressure vessels, ship parts and other heavy machinery parts.
Metalforming technology used for final shaping of large ingots is Forging.
The largest ingot (570 metric tons) was produced in 1980 by “Kawasaki Steel” (Japan).
Solidification of a large mass of steel is characterized by significant development of micro and macro-defects of the ingot structure:
The structure defects decrease the reliability of the part manufactured from the ingot. Since such parts work in equipment, failure of which is potentially catastrophic (nuclear equipment, electric power plants, chemical equipment, large scale machinery), Technology of large ingots fabrication should provide minimum degree of steel structure defects.
Non-metallic inclusions in steel are chemical compounds of metals (Fe, Mn, Al, Si, Ca) with non-metals (O, S, C, H, N). Non-metallic inclusions form separate phases. The non-metallic phases containing more than one compound (eg. different oxides, oxide+sulfide) are called complex non-metallic inclusions (spinels, oxysulfides, carbonitrides).
Despite small content of non-metallic inclusions in steel (0.01-0.02%) they exert significant effect on the steel properties such as:
The following parameters of non-metallic inclusions influence on the properties of parts made of large steel ingots:
Size of non-metallic inclusions is determined by the processes of nucleation, growth and coalescence/agglomeration. High surface energy causes the nucleation at higher supersaturation of the solutes (oxygen, sulfur, nitrogen, aluminum, silicon, titanium, vanadium, etc.) and favors coalescence and agglomeration of the inclusions.
Homogeneous distribution of non-metallic inclusions is most desirable. Clusters of inclusions are unfavorable since they may result in local drop of mechanical properties such as toughness and fatigue strength.
Microscopic hard inclusions (carbides, nitrides) strengthen the metal however larger hard inclusions may cause drop of the steel ductility without increase of the strength and hardness. Ductile and brittle inclusions behave different during plastic deformation (steel Forging). Ductile inclusions elongate in the direction of deformation. Brittle inclusions break to fragments and form chains.
The following factors favors macrosegregation in large steel ingots:
Development of macrosegregation zones in a steel ingot and their locations are associated with the ingot grain structure.
Bottom negative segregation is a result of low solute concentration in the crystals formed in the early stage of solidification and comprising bottom cone. The bottom cone is a mixture of small equiaxed garins grown as a result of the contact with a bottom of a cold metallic mold and crystals and crystals fragments, which sedimintate from other ingot zones.
The central zone of ingot is enriched with solute rejected by the solidification front progressing from the mold wall to its center. The central zone consists of large equiaxed grains, which settle down to the V-shaped solidification front. The residual liquid surrounding the large equiaxed grains is solute-rich and it forms V-segregates when solidifies.
A-segregates (freckles) form in the Zone of columnar grains at the regions with structure characterized by the transition from the columnar grains to large equiaxed grains. A-segrgates present channels enriched by sulfur, carbon, phosphorus and other impurities.
Hot top segregation zone is located in the top central ingot region below the shrinkage cavity. Hot top segregation is formed at the final solidification stage from the residual liquid enriched by the solutes as a result of microsegregation (rejection by solidifying dendrites) followed by penetration of the liquid through the dendrite skeleton.
Factors allowing to diminish macrosegregation in large steel ingots:
Sources of hydrogen in liquid steel:
Hydrogen is easily dissolved in liquid steel in dissociated (atomic) state. Solubility of hydrogen in steel drops sharply during solidification resulting in formation of gaseous hydrogen form H2. In solid steel hydrogen is dissolved in form of interstitial solution.
Carbon, nickel, chromium (up to 10%), vanadium, titanium, zirconium, columbium, tantalum increase the solubility of hydrogen in solid steel.
Silicon, aluminum, tungsten, chromium (10% and higher) decrease the solubility of hydrogen in solid steel.
Solubility of hydrogen in austenite is much higher than in ferrite.
Both gaseous and dissolved forms of hydrogen exert adverse effect on mechanical properties of steels:
Solubility of hydrogen decrease during solidification and cooling down of steel ingot. Hydrogen atoms possessing high mobility are collected at internal voids such as non-metallic inclusions (sulfides, oxides) and their clusters, shrinkage pores, cracks caused by internal stresses.
Hydrogen atoms collected at internal voids combine and form gaseous hydrogen H2, which may cause formation of cracks (flakes) when the gas pressure exceeds the steel strength.
Hydrogen flakes is particularly dangerous for parts fabricated from large ingots. Vacuum ladle degassing methods allow to decrease the content of hydrogen to 2 ppm, which does not cause flaking formation.
Hydrogen in dissolved form also decreases steel properties such as ductility, Fracture Toughness and fatigue strength.
The following tasks are accomplished by the technology of large ingots fabrication:
The possible technological schemes of large steel ingots fabrication are presented in the figure:
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