Disclosed is a steel composition including specified ranges of Ni; Mo; Co; Mo+Co+Si+Mn+Cu+W+V+Nb+Zr+Ta+Cr+C; Co+Mo; Ni+Co+Mo; and traces of Al; Ti; N; Si; Mn; C; S; P; B; H; O; Cr; Cu; W; Zr; Ca; Mg; Nb; V; and Ta in specified ranges; the remainder being iron and impurities. The inclusion population, as observed by image analysis over a polished surface measuring 650 mm.sup.2 if hot-formed or hot-rolled; and measuring 800 mm.sup.2 if cold-rolled, does not contain non-metallic inclusions of diameter>10 μm, and, in the case of a hot-rolled sheet, does not contain more than four non-metallic inclusions of diameter 5-10 μm over 100 mm.sup.2, the observation being performed by image analysis over a polished surface measuring 650 mm.sup.2.

A rack bar includes: a rack tooth row including a plurality of rack teeth meshing with pinion teeth; a hardened layer provided continuously over an entire circumference of the rack tooth row; and a center portion provided inside the hardened layer and having lower hardness than the hardened layer. When the rack bar is viewed in an axial direction of the rack bar, a depth of the hardened layer from the following positions i), ii), and iii) increases in this order: i) a bottom land of the rack teeth; ii) a side of the rack bar relative to the bottom land; and iii) a back of the rack bar relative to the bottom land.

The invention relates to a method for the impact treatment of transition radii (8) of a crankshaft (4, 4′), in particular transition radii (8) between connecting rod bearing journals (5, 5′) and crank webs (7, 7′) and/or transition radii (8) between main bearing journals (6, 6′) and the crank webs (7, 7′) of the crankshaft (4, 4′). The crankshaft (4, 4′) is then rotated along a rotational direction into an impact position by means of a drive device (3, 3′). A locking device (12) is provided in order to lock the crankshaft (4, 4′) in the impact position, and an impact force is then introduced into at least one transition radius (8) by at least one impact tool (16, 16′).

A method for controlling deformation of a large-scale crankshaft comprising detecting and recording stress value(s) of part(s) to be regulated by the crankshaft; fixing the crankshaft on a tool to couple transmitting ends of high-energy acoustic beam transducers with the part(s) to be regulated; turning on the high-energy acoustic beam transducers to emit high-energy acoustic beams into the crankshaft, controlling working frequencies of the high-energy acoustic beam transducers within a range of 10-30 kHz, and setting a predicted regulation and control time according to the stress value(s) of the part(s) to be regulated; and closing the high-energy acoustic beam transducers when the predicted regulation and control time is reached, and taking the crankshaft out of the tool.

A method for controlling deformation of a large-scale crankshaft comprising detecting and recording stress value(s) of part(s) to be regulated by the crankshaft; fixing the crankshaft on a tool to couple transmitting ends of high-energy acoustic beam transducers with the part(s) to be regulated; turning on the high-energy acoustic beam transducers to emit high-energy acoustic beams into the crankshaft, controlling working frequencies of the high-energy acoustic beam transducers within a range of 10-30 kHz, and setting a predicted regulation and control time according to the stress value(s) of the part(s) to be regulated; and closing the high-energy acoustic beam transducers when the predicted regulation and control time is reached, and taking the crankshaft out of the tool.

The present invention refers to a method for repairing a component, in particular a component of an internal combustion engine, by heat treating, in particular tempering. The method comprises a step of obtaining a material specific reference parameter which has been determined based on at least one reference test carried out on a reference sample made of the same material as the component to be heat treated, wherein the reference parameter is indicative of a desired heat treating effect on the material of the component to be heat treated; a step of determining at least one of a heating temperature and heating duration in dependence on the obtained reference parameter; and a step of heat treating the component in accordance with at least one of the determined heating temperature and determined heating duration.

Provided are a roughly-shaped steel material for a nitrided part, and a nitrided part obtained by nitriding the roughly-shaped steel material for a nitrided part, having a determined chemical composition, in which the portion with a diameter or width ranging from 60 to 130 mm of the roughly-shaped steel material for a nitrided part has a microstructure at a depth of 14.5 mm from a surface including, in terms of area fraction: tempered martensite and tempered bainite in total: from 70 to 100%; remaining austenite: from 0 to 5%; and a balance: ferrite and perlite; and has a microstructure at a depth of 15 mm or more from the surface including, in terms of area fraction: tempered martensite and tempered bainite in total: from 0 to less than 50%; remaining austenite: from 0 to 5%; and a balance: ferrite and perlite.

Provided are a roughly-shaped steel material for a nitrided part, and a nitrided part obtained by nitriding the roughly-shaped steel material for a nitrided part, having a determined chemical composition, in which the portion with a diameter or width ranging from 60 to 130 mm of the roughly-shaped steel material for a nitrided part has a microstructure at a depth of 14.5 mm from a surface including, in terms of area fraction: tempered martensite and tempered bainite in total: from 70 to 100%; remaining austenite: from 0 to 5%; and a balance: ferrite and perlite; and has a microstructure at a depth of 15 mm or more from the surface including, in terms of area fraction: tempered martensite and tempered bainite in total: from 0 to less than 50%; remaining austenite: from 0 to 5%; and a balance: ferrite and perlite.

A non-heat treated steel for induction hardening contains, in mass %, C: 0.35 to 0.44%, Si: 0.01 to less than 0.30%, Mn: 0.80 to 1.50%, P: 0.030% or less, S: more than 0.010 to 0.095%, Cr: more than 0.10 to 0.30%, V: 0.050 to 0.200%, N: 0.0040 to 0.0200%, O: 0.0024% or less, Cu: 0.05% or less and Ni: 0.05% or less, and for which fn1≤50.0, fn2: 0.70 to 1.00, and fn3≥1.30. In the steel, a ratio of a number of Mn oxides containing oxygen in an amount of 20.0 mass % or more and Mn in an amount of 10.0 mass % or more to the number of oxides is 10.0% or less
fn1=80C.sup.2+55C+13Si+4.8Mn+30P+30S+1.5Cr
fn2=C+(Si/10)+(Mn/5)−(5S/7)+(5Cr/22)+1.65V
fn3=−2C—Si+2.33Mn+0.26Cr+V−1.5Cu−1.5Ni.

A non-heat treated steel for induction hardening contains, in mass %, C: 0.35 to 0.44%, Si: 0.01 to less than 0.30%, Mn: 0.80 to 1.50%, P: 0.030% or less, S: more than 0.010 to 0.095%, Cr: more than 0.10 to 0.30%, V: 0.050 to 0.200%, N: 0.0040 to 0.0200%, O: 0.0024% or less, Cu: 0.05% or less and Ni: 0.05% or less, and for which fn1≤50.0, fn2: 0.70 to 1.00, and fn3≥1.30. In the steel, a ratio of a number of Mn oxides containing oxygen in an amount of 20.0 mass % or more and Mn in an amount of 10.0 mass % or more to the number of oxides is 10.0% or less
fn1=80C.sup.2+55C+13Si+4.8Mn+30P+30S+1.5Cr
fn2=C+(Si/10)+(Mn/5)−(5S/7)+(5Cr/22)+1.65V
fn3=−2C—Si+2.33Mn+0.26Cr+V−1.5Cu−1.5Ni.