Classifications

• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
  • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/26—Methods of annealing
  • C21D1/28—Normalising
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2201/00—Treatment for obtaining particular effects
  • C21D2201/05—Grain orientation

Definitions

• the present invention relates to a bar-shaped steel product.
• Small-diameter wire rods made of a high purity ferrite stainless steel are conventionally used to produce cold forging parts.
• large-diameter wire rods, steel bars, and the like made of the high purity ferrite stainless may have restriction on cold forging. This is because in the large-diameter wire rods and steel bars made of the high purity ferrite stainless steel, coarse unrecrystallized crystal grains and the like in a steel structure are present to decrease toughness and promote brittle fracture during cold forging.
• Patent Literatures 1 to 6 disclose steel wire rods and the like whose properties are improved by appropriately controlling chemical compositions, manufacturing conditions and the like.
• an object of the invention is to solve the above problem and provide a bar-shaped steel product having an excellent toughness.
• the invention has been made for solving the above problem and provides a bar-shaped steel product below as a gist.
• the bar-shaped steel product according to the above aspects of the invention is exemplified by a steel wire rod, a steel wire, and a steel bar.
• a crystal orientation of a rolling direction is controlled.
• a rolling-direction-crystal-orientation RD// ⁇ 100> fraction (area ratio) (hereinafter, simply referred to as a "RD// ⁇ 100> fraction") is preferably 0.5 or less. This is because the RD// ⁇ 100> fraction exceeding 0.5 promotes brittle fracture and decreases toughness.
• the RD// ⁇ 100> fraction is more preferably 0.40 or less, further preferably 0.35 or less.
• the RD// ⁇ 100> fraction is calculated according to the following procedure. Specifically, the RD// ⁇ 100> fraction is obtained by measuring at least one field of view among 200-fold fields of view in a surface layer portion, a center portion, and a 1/4-depth-position existing between the surface layer portion and the center portion in an L-cross section of a steel product (i.e., a cross section including a center of the steel product and being in parallel to the rolling direction (longitudinal direction) of the steel product).
• a crystal orientation of each of crystal grains in the observed field(s) of view is analyzed using FE-SEM/EBSD.
• the rolling direction is represented by RD.
• a crystal plane in the RD direction is analyzed.
• the surface layer portion refers to a position at a 1-mm depth in a central axial direction from a surface of the steel product.
• the rolling-direction-crystal-orientation RD// ⁇ 100> fraction means an area ratio of crystal having 20 degrees or less of an orientation difference between the ⁇ 100> orientation and the rolling direction.
• a C content is defined at 0.001% or more, preferably 0.002% or more.
• an excessive C content increases the RD// ⁇ 100> fraction.
• the C content is defined at 0.09% or less.
• the C content is preferably 0.05% or less, more preferably 0.03% or less, further preferably 0.02% or less.
• Si is contained as a deoxidizing element to improve high-temperature oxidation properties. For this reason, an Si content is defined at 0.01% or more, preferably 0.05% or more. However, an excessive Si content increases the RD// ⁇ 100> fraction. As a result, toughness is decreased. For this reason, the Si content is defined at 3.0% or less.
• the Si content is preferably 2.0% or less, more preferably 1.0% or less, further preferably 0.5% or less.
• Mn improves strength of the steel product. For this reason, an Mn content is defined at 0.01% or more, preferably 0.05% or more. However, an excessive Mn content increases the RD// ⁇ 100> fraction. As a result, toughness is decreased. Moreover, corrosion resistance is sometimes decreased. For this reason, the Mn content is defined at 2.0% or less.
• the Mn content is preferably 1.0% or less, more preferably 0.8% or less, further preferably 0.5% or less.
• Ni improves the toughness of the steel product. For this reason, an Ni content is defined at 0.01% or more, preferably 0.05% or more. However, an excessive Ni content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the Ni content is defined at 5.0% or less.
• the Ni content is preferably 2.0% or less, more preferably 1.0% or less, further preferably 0.5% or less.
• the Cr content is defined at 7.0% or more.
• the Cr content is preferably 10.0% or more, more preferably 15.0% or more.
• an excessive Cr content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased.
• the Cr content is defined at 35.0% or less.
• the Cr content is preferably 27.0% or less, more preferably 25.0% or less, further preferably 21.0% or less.
• Mo improves the corrosion resistance. For this reason, an Mo content is defined at 0.01% or more. However, an excessive Mo content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the Mo content is defined at 5.0% or less.
• the Mo content is preferably 2.0% or less, more preferably 1.0% or less, further preferably 0.5% or less.
• Cu improves the corrosion resistance. For this reason, a Cu content is defined at 0.01% or more, preferably 0.30% or more. However, an excessive Cu content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the Cu content is defined at 3.0% or less.
• the Cu content is preferably 2.0% or less, more preferably 1.0% or less, further preferably 0.5% or less.
• N increases the strength of the steel product. For this reason, an N content is defined at 0.001% or more, preferably 0.004% or more. However, an excessive N content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the N content is defined at 0.10% or less.
• the N content is preferably 0.05% or less, more preferably 0.03% or less, further preferably 0.02% or less.
• Nb has an effect of increasing the strength of the steel product. Moreover, since Nb forms carbonitrides, formation of Cr carbides is suppressed to suppress formation of Cr-deficient layers. As a result, Nb has an effect of preventing intergranular corrosion. In other words, since Nb is an effective element for improving the corrosion resistance, an Nb content to be added is 0.2% or more, preferably 0.3% or more. However, an excessive Nb content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Moreover, coarse carbonitrides decrease the toughness. For this reason, the Nb content is defined at 2.0% or less. The Nb content is preferably 1.0% or less, more preferably 0.8% or less.
• the bar-shaped steel product of the invention may contain at least one element selected from Ti, V, B, Al, W, Ga, Co, Sn, and Ta as needed, in addition to the aforementioned elements.
• Ti has an effect of increasing the strength of the steel product. Moreover, since Ti forms carbonitrides, formation of Cr carbides is suppressed to suppress formation of Cr-deficient layers. As a result, Ti has an effect of preventing intergranular corrosion. In other words, since Ti has an effect of improving the corrosion resistance, Ti may be contained as needed.
• the Ti content is defined at 2.0% or less.
• the Ti content is preferably 1.0% or less, more preferably 0.5% or less, further preferably 0.05% or less.
• the Ti content is preferably 0.001% or more in order to obtain the aforementioned effects.
• V has the effect of improving the corrosion resistance
• V may be contained as needed.
• an excessive V content increases the RD// ⁇ 100> fraction.
• the toughness is decreased.
• coarse carbonitrides decrease the toughness.
• the V content is defined at 2.0% or less.
• the V content is preferably 1.0% or less, more preferably 0.5% or less, further preferably 0.1% or less.
• the V content is preferably 0.001% or more in order to obtain the aforementioned effects.
• B has effects of improving hot workability and corrosion resistance. Accordingly, B may be contained as needed. However, an excessive B content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the B content is defined at 0.1% or less.
• the B content is preferably 0.02% or less, more preferably 0.01% or less.
• the B content is preferably 0.0001% or more in order to obtain the aforementioned effects.
• Al Since Al has an effect of promoting deoxidation to improve a cleanliness level of inclusions, Al may be contained as needed. However, an excessive Al content saturates this effect and increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Moreover, coarse inclusions decrease the toughness. For this reason, the Al content is defined at 5.0% or less.
• the Al content is preferably 1.0% or less, more preferably 0.1% or less, further preferably 0.01% or less.
• the Al content is preferably 0.001% or more in order to obtain the aforementioned effects.
• W Since W has the effect of improving the corrosion resistance, W may be contained as needed. However, an excessive W content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Moreover, coarse carbonitrides decrease the toughness. For this reason, the W content is defined at 2.5% or less.
• the W content is preferably 2.0% or less, more preferably 1.5% or less.
• the W content is preferably 0.05% or more, more preferably 0.10% or more.
• Ga has the effect of improving the corrosion resistance
• Ga may be contained as needed.
• an excessive Ga content decreases the hot workability.
• the Ga content is defined at 0.05% or less.
• the Ga content is preferably 0.0004% or more in order to obtain the aforementioned effects.
• Co Since Co has the effect of improving the strength of the steel product, Co may be contained as needed. However, an excessive Co content increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. For this reason, the Co content is defined at 2.5% or less.
• the Co content is preferably 1.0% or less, more preferably 0.8% or less.
• the Co content is preferably 0.05% or more, more preferably 0.10% or more.
• the Sn content is defined at 2.5% or less.
• the Sn content is preferably 1.0% or less, more preferably 0.2% or less.
• the Sn content is preferably 0.01% or more, more preferably 0.05% or more.
• Ta has the effect of improving the corrosion resistance
• Ta may be contained as needed.
• an excessive Ta content increases the RD// ⁇ 100> fraction.
• the toughness is decreased.
• the Ta content is defined at 2.5% or less.
• the Ta content is preferably 1.5% or less, more preferably 0.9% or less.
• the Ta content is preferably 0.01% or more, more preferably 0.04% or more, further preferably 0.08% or more.
• the bar-shaped steel product of the invention may contain at least one element selected from Ca, Mg, Zr, and REM as needed, in addition to the aforementioned elements.
• Ca, Mg, Zr, and REM may be contained for deoxidation, as needed.
• an excessive content of each of Ca, Mg, Zr, and REM increases the RD// ⁇ 100> fraction.
• the toughness is decreased.
• coarse inclusions decrease the toughness.
• Ca of 0.05% or less, Mg of 0.012% or less, Zr of 0.012% or less, and REM of 0.05% or less are defined.
• the Ca content is preferably 0.010% or less, more preferably 0.005% or less.
• the Mg content is preferably 0.010% or less, more preferably 0.005% or less.
• the Zr content is preferably 0.010% or less, more preferably 0.005% or less.
• REM is preferably 0.010% or less.
• Ca of 0.0002% or more, Mg of 0.0002% or more, Zr of 0.0002% or more, and REM of 0.0002% or more are preferable.
• the Ca content is more preferably 0.0004% or more, further preferably 0.001% or more.
• the Mg content is more preferably 0.0004% or more, further preferably 0.001% or more.
• the Zr content is more preferably 0.0004% or more, further preferably 0.001% or more.
• the REM content is more preferably 0.0004% or more, further preferably 0.001% or more.
• REM is a general term for 17 elements including Y, Sc, and 15 elements of lanthanoids. One or more of the 17 elements can be contained in steel. The REM content means a total content of these elements.
• a balance consists of Fe and inevitable impurities.
• the "inevitable impurities” herein mean substances in raw materials such as ore and scrap as well as components mixed in the manufacturing process due to various factors when the steel sheet is industrially manufactured, the substances and the components being allowable within a range that does not adversely affect the invention.
• Examples of the inevitable impurities include S, P, O, Zn, Bi, Pb, Se, Sb, H, and Te.
• the inevitable impurities are preferably reduced, however, when being contained, Zn, Bi, Pb, Se, and H are desirably 0.01% or less.
• Sb and Te are desirably 0.05% or less.
• a cross section perpendicular to a length direction is not particularly limited.
• the cross section is not limited only to a general circular cross section.
• the bar-shaped steel product can be exemplified by a deformed bar as well as a flat steel bar and a square steel bar whose cross sections are rectangular.
• a diameter of the cross section is preferably in a range from 15.0 to 200 mm.
• the diameter of the cross section is preferably 15.0 mm or more, more preferably 20.0 mm or more, further preferably 30.0 mm or more.
• the diameter of the cross section exceeding 200 mm increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased.
• the diameter of the cross section is preferably 200 mm or less.
• the diameter of the cross section is more preferably 150 mm or less, further preferably 100 mm or less, particularly preferably 70 mm or less.
• the bar-shaped steel product according to the invention is evaluated in terms of toughness using a ductile-brittle transition temperature according to Charpy impact test.
• the toughness is evaluated as being favorable when the transition temperature is 200 degrees C or less.
• the transition temperature is preferably 150 degrees C or less, more preferably 100 degrees C or less, further preferably 80 degrees C or less, still further preferably 30 degrees C or less.
• a favorable lower limit of the transition temperature is defined as -150 degrees C due to components used for controlling a texture, and costs caused by manufacturing restriction.
• a favorable manufacturing method of the bar-shaped steel product according to the invention will be described.
• a steel wire rod having a circular cross section will be described as an example.
• the bar-shaped steel product according to the invention can provide the effects as long as having the aforementioned structure irrespective of the manufacturing method.
• the bar-shaped steel product according to the invention is stably obtainable according to, for instance, a manufacturing method below.
• the bar-shaped steel product according to the invention it is preferable to melt steel having the aforementioned chemical composition, cast the molten steel into a cast piece having a predetermined diameter, and then subject the cast piece to hot rolling or warm rolling for a wire rod. Subsequently, it is preferable to appropriately perform a solution treatment and pickling as needed.
• a heating temperature of the cast piece is related to a processing temperature and contributes to cumulative strain and recrystallization behavior of the bar-shaped steel product, and eventually changes a RD// ⁇ 100> fraction, which is related to toughness. Therefore, it is preferable to heat the cast piece, which is obtained by melting and casting, at a temperature in a range from 450 to 1300 degrees C. An excessively low heating temperature of the cast piece embrittles the bar-shaped steel product. Therefore, the heating temperature of the cast piece is preferably 450 degrees C or more, more preferably 700 degrees C or more, further preferably 800 degrees C or more.
• the heating temperature of the cast piece is preferably 1300 degrees C or less, more preferably 1200 degrees C or less, further preferably 1100 degrees C or less.
• the heated cast piece is subjected to hot working by using skew rolling.
• the hot working is not limited to the skew rolling. Any method of hot working going through the same or similar heat processing history is usable. For instance, blooming (breakdown) is usable as long as going through the same or similar heat processing history.
• a reduction of area in the skew rolling changes the RD// ⁇ 100> fraction. Therefore, the reduction of area affects toughness.
• the reduction of area of less than 20.0% increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the reduction of area is preferably 20.0% or more, more preferably 40.0% or more, further preferably 50.0% or more, still further preferably 80.0% or more.
• a processing temperature in the skew rolling (i.e., a temperature of the steel product after the skew rolling) changes the RD// ⁇ 100> fraction. Since the processing temperature in the skew rolling thus affects the toughness, the processing temperature is preferably in a range from 450 to 1200 degrees C. When the processing temperature in the skew rolling is less than 450 degrees C, the steel product is embrittled. Therefore, the processing temperature in the skew rolling is preferably 450 degrees C or more, more preferably 700 degrees C or more. However, the processing temperature exceeding 1200 degrees C in the skew rolling increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the processing temperature in the skew rolling is preferably 1200 degrees C or less, more preferably 1100 degrees C or less, further preferably 1000 degrees C or less.
• the steel product is preferably subjected to intermediate annealing.
• a time from the completion of the skew rolling to the start of the intermediate annealing changes the RD// ⁇ 100> fraction. Therefore, the time from the completion of the skew rolling to start of the intermediate annealing affects the toughness.
• the time from the completion of the skew rolling to the start of the intermediate annealing is preferably in a range from 0.01 to 100 s.
• the time from the completion of the skew rolling to start of the intermediate annealing is less than 0.01 s, the RD// ⁇ 100> fraction is increased in the later-described manufacturing step. As a result, the toughness is decreased. Therefore, the time from the completion of the skew rolling to start of the intermediate annealing is preferably 0.01 s or more, more preferably 0.1 s or more, further preferably 1 s or more.
• the time from the completion of the skew rolling to start of the intermediate annealing exceeds 100 s, the RD// ⁇ 100> fraction is increased. As a result, the toughness is decreased. Therefore, the time from the completion of the skew rolling to start of the intermediate annealing is preferably 100 s or less, more preferably 50 s or less, further preferably 10 s or less.
• the subsequent intermediate annealing step is performed in order to recrystallize a coarse solidified texture formed by casting.
• it is preferably to anneal the steel product in a temperature range from 700 to 1300 degrees C. Recrystallization of the steel product in the intermediate annealing step decreases the RD// ⁇ 100> fraction. As a result, the toughness is improved.
• a temperature in the intermediate annealing hereinafter, referred to as a "intermediate annealing temperature”
• the RD// ⁇ 100> fraction is increased.
• the toughness is decreased. Therefore, the intermediate annealing temperature is preferably 700 degrees C or more, more preferably 800 degrees C or more.
• the intermediate annealing temperature exceed 1300 degrees C increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the intermediate annealing temperature is preferably 1300 degrees C or less, more preferably 1200 degrees C or less, further preferably 1100 degrees C or less.
• An annealing time in the intermediate annealing (hereinafter, referred to as an "intermediate annealing time”) is preferably in a range from 1 to 480 min.
• the intermediate annealing time of less than 1 min increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the intermediate annealing time is preferably 1 min or more, more preferably 30 min or more.
• the intermediate annealing time exceeding 480 min increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the intermediate annealing time is preferably 480 min or less, more preferably 180 min or less.
• the rolling is performed using a skew rolling mill, rough rolling mill, intermediate rolling mill, finish rolling mill and/or the like.
• a total reduction of area by the rolling including the above skew rolling, and the like refers to a reduction of area until an entire processing is completed.
• the total reduction of area changes the RD// ⁇ 100> fraction. Therefore, the total reduction of area affects the toughness.
• the total reduction of area of less than 30.0% increases the RD// ⁇ 100> fraction. As a result, the toughness is decreased. Therefore, the total reduction of area is preferably 30.0% or more, more preferably 50.0% or more, further preferably 80.0% or more, still further preferably 90.0% or more.
• the roller diameter of the rough rolling mill is preferably in a range from 200 to 2500 mm.
• the roller diameter of the rough rolling mill is less than 200 mm, shear deformation is promoted in the steel product to form an orientation other than RD// ⁇ 110> that is a priority orientation of the deformed texture of BCC crystal structure, thereby increasing the RD// ⁇ 100> fraction.
• a plane perpendicular to the ⁇ 100> orientation is a cleavage plane, the increase of the RD// ⁇ 100> fraction decreases the toughness.
• the roller diameter of the rough rolling mill is 200 mm or more, preferably 400 mm or more.
• the roller diameter of the rough rolling mill exceeds 2500 mm, rolling equipment becomes large, which is uneconomical. Accordingly, the roller diameter of the rough rolling mill is defined at 2500 mm or less, ⁇ nret>> preferably 2000 mm or less, further preferably 1500 mm or less.
• the cast piece was heated at a heating temperature of 1030 degrees C, was subjected to the skew rolling at a reduction of area of 80.0% and a processing temperature of 805 degrees C, and, subsequently, was subjected to the intermediate annealing at an annealing temperature of 960 degrees C for an annealing time of 3.5 min. In this operation, a time between the skew rolling and the intermediate annealing was 5.4 s. Subsequently, the steel was rolled. For the rolling, a roller diameter for rough rolling was 940 mm, a rolling temperature was 750 degrees C, a rolling finish temperature was 730 degrees C, and a time between rolling passes was 0.5 s.
• the total reduction of area was 93.2%.
• the rolled steel was cooled at a cooling rate of 11 degrees C/s, was subjected to final annealing at a final annealing temperature of 750 degrees C for a final annealing time of 0.8 min, and was cooled at a cooling rate of 14 degrees C/s.
• the obtained steel wire rod was measured in terms of the RD// ⁇ 100> fraction and a transition temperature. Results are collectively shown in Tables 3 and 4 below. The measurements were performed according to the following procedure.
• the RD// ⁇ 100> fraction was obtained by measuring at least one field of view among 200-fold fields of view in a surface layer portion, a center portion, and a 1/4-depth-position existing between the surface layer portion and the center portion in an L-cross section of a steel product.
• a crystal orientation of each of crystal grains in the observed field(s) of view was analyzed using FE-SEM/EBSD.
• a rolling direction was represented by RD.
• a crystal plane in the RD direction was analyzed. Components in a ⁇ 001> orientation only in a clearance of 20 degrees or less were displayed and the RD// ⁇ 100> fraction was measured.
• a transition temperature was a ductile-brittle transition temperature in Charpy impact test in accordance with JIS Z 2242.
• a test piece in the Charpy impact test was a standard test piece.
• a length direction of the test piece was a rolling direction of the bar-shaped steel product.
• a notch of the test piece was U-notch.
• An energy transition temperature was used as the ductile-brittle transition temperature. The toughness was judged as being favorable when the transition temperature was 200 degrees C or less.
• Nos. 1 to 37 satisfied the requirement of the invention, exhibiting a favorable toughness.
• Nos. 38 to 52 not satisfying the requirement of the invention exhibited a poor toughness and a poor corrosion resistance.
• steel types O and V shown in Table 1 were molten in the same manner and casted into cast pieces having various diameters. Subsequently, the cast pieces were heated at a heating temperature of 1053 degrees C, was subjected to the skew rolling at a reduction of area of 63.2% and a processing temperature of 948 degrees C, and then was annealed at an annealing temperature of 1032 degrees C for an annealing time of 1.6 min. In this operation, a time between the skew rolling and the annealing was 3 s. Subsequently, the steels were rolled.
• a roller diameter for rough rolling was 880 mm
• a rolling temperature was 940 degrees C
• a rolling finish temperature was 835 degrees C
• a time between rolling passes was 6 s.
• the total reduction of area by the rolling was 83.0%.
• the rolled steels were cooled at a cooling rate of 12 degrees C/s, were subjected to final annealing at a final annealing temperature of 1040 degrees C for a final annealing time of 1.4 min, and were cooled at a cooling rate of 12 degrees C/s.
• the obtained bar-shaped steel products were measured according to the above-mentioned method in terms of the RD// ⁇ 100> fraction and the transition temperature. Results are collectively shown in Table 5 below. As described above in Example 1, the toughness was judged as being favorable when the transition temperature was 200 degrees C or less.
• Nos.53 to 75 satisfied the requirement of the invention, exhibiting a favorable toughness.
• a steel type Q shown in Table 1 was used to provide cast pieces having various diameters, from which bar-shaped steel products each having a diameter of 15 mm were manufactured under conditions shown in Tables 6 and 7.
• the manufactured bar-shaped steel products were measured according to the above-mentioned method in terms of the RD// ⁇ 100> fraction and the transition temperature. Results are collectively shown in Tables 6 and 7 below.
• the toughness was judged as being favorable when the transition temperature was 200 degrees C or less.
• a bar-shaped steel product having an excellent toughness is obtainable and extremely useful in industry.

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