WO2014034070A1 - Steel for reinforcing bars, and reinforcing bar - Google Patents
Steel for reinforcing bars, and reinforcing bar Download PDFInfo
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- WO2014034070A1 WO2014034070A1 PCT/JP2013/004997 JP2013004997W WO2014034070A1 WO 2014034070 A1 WO2014034070 A1 WO 2014034070A1 JP 2013004997 W JP2013004997 W JP 2013004997W WO 2014034070 A1 WO2014034070 A1 WO 2014034070A1
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- 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
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- 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
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- 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
- C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
- C21D3/02—Extraction of non-metals
- C21D3/04—Decarburising
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- 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
- C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
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- 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
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- 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
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- 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
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- 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
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- 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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- E—FIXED CONSTRUCTIONS
- E04—BUILDING
- E04C—STRUCTURAL ELEMENTS; BUILDING MATERIALS
- E04C5/00—Reinforcing elements, e.g. for concrete; Auxiliary elements therefor
- E04C5/01—Reinforcing elements of metal, e.g. with non-structural coatings
Definitions
- the present invention relates to, for example, a high-strength reinforcing bar used as a shear reinforcement used in a reinforced concrete structure and a steel for reinforcing steel used as a material thereof.
- reinforced concrete structures such as buildings and apartment houses use shear reinforcement as a reinforcing material to prevent their collapse.
- shear reinforcement when the reinforced concrete structure undergoes shear deformation, the shear reinforcement stretches and plastically deforms, so that the deformation energy of the reinforced concrete structure is absorbed by the shear reinforcement and the reinforced concrete structure Collapse is prevented.
- a shear reinforcing bar having a tensile strength of about 1200 MPa is generally used.
- a shear reinforcing bar having a tensile strength of about 1200 MPa is generally used.
- the shear reinforcement bar functions as a reinforcing material by wrapping it around the main bar that prevents the shaft that supports the structure of the building from bending, such as concrete columns and beams, for example.
- the cross section is shaped into a coil shape such as a circle or a square. Since these cross-sectional shapes are given by bending, bending workability is required for the molding. Therefore, if the shear reinforcement has excellent elongation characteristics, bending work becomes easy, which is a great advantage in terms of workability.
- the strength of the shear reinforcement is increased in accordance with the increase in the strength of the concrete, there are newly concerns about problems such as breakage during bending.
- the shear reinforcing bars are generally manufactured by drawing steel for reinforcing bars and then performing heat treatment. Therefore, when the addition amount of the alloy element is increased, the hardness of the steel for reinforcing bars is increased, the wire is disconnected when the steel for reinforcing bars is drawn, and the productivity is lowered. Therefore, in order to achieve high strength, it was necessary to avoid a decrease in the drawability of the steel for reinforcing bars.
- Patent Document 1 discloses a heat treatment method in which C, Si, and Mn are controlled within an appropriate range, and cooling conditions are controlled to ensure a surface decarburization of 0.12 mm or more.
- C, Si, and Mn are controlled within an appropriate range, and cooling conditions are controlled to ensure a surface decarburization of 0.12 mm or more.
- the ferrite decarburization is 0.12 mm or more, it is difficult to ensure the strength when a high-strength reinforcing bar is manufactured. Therefore, it is necessary to increase the strength other than the ferrite decarburized layer, and it is necessary to add an alloy. Therefore, the hardness of the material for reinforcing bars is increased, and the drawability is lowered.
- the toughness of the reinforcing bar is lowered and the bending workability is lowered.
- Patent Document 2 the amount of C, Si, Mn, Ni, and Al is optimized, the ferrite decarburized layer on the steel surface layer is controlled to 0.12 mm or more, and the inside is controlled to a ferrite pearlite structure or a spheroidized cementite structure.
- a steel wire having excellent delayed fracture characteristics is obtained.
- the ferrite decarburization is 0.12 mm or more, it is difficult to ensure the strength when a high-strength reinforcing bar is manufactured, so it is necessary to increase the strength other than the ferrite decarburized layer, and an alloy addition is necessary. Become.
- the hardness of the material for the reinforcing bars is increased and the wire drawing property is decreased, or the toughness of the reinforcing bars is decreased after manufacturing the high-strength reinforcing bars, and the bending workability is decreased.
- the wire rod rolling it is necessary to perform heat treatment online or offline, which increases extra operation costs such as reheating.
- Patent Document 3 discloses a high-strength reinforcing bar in which the component composition and the ferrite area ratio and the total area ratio of ferrite and pearlite structure are controlled. However, when the pearlite structure is generated, the toughness is lowered, so that the bending workability may be lowered.
- Patent Document 4 discloses a method for producing high-strength steel with high yield elongation by controlling the component composition and rolling method.
- the tensile strength is 100 kg / mm 2 or less, and when the strength is increased, the yield elongation decreases, so the bending workability may decrease.
- Patent Document 5 discloses a method for producing a high-strength steel with high yield elongation by controlling the component composition and the rolling method. As described above, since the yield elongation decreases when the strength is increased, the bending workability may also decrease.
- the present invention has been made to solve such a problem, and provides a steel for reinforcing bars that can produce a reinforcing bar having high strength and excellent bending workability under excellent wire drawing. With the goal.
- the inventors manufactured high-strength steel for reinforcing bars with various amounts of addition of C, Si, Mn, Cr and Mo, and made the wire drawing property and hardness of the steel for reinforcing steel (drawing). Hard investigation of the hardness of the previous material.
- the steel for high-strength reinforcing steel was drawn and subjected to heat treatment, and the tensile strength and bending workability of the high-strength reinforcing steel produced by conducting heat treatment were intensively investigated.
- the gist configuration of the present invention is as follows. 1. C: 0.37 mass% or more and 0.50 mass% or less, Si: 1.75% by mass to 2.30% by mass, Mn: 0.2% by mass or more and 1.0% by mass or less, Cr: 0.01% by mass or more and 1.2% by mass or less Mo: 0.05% by mass or more and 1.0% by mass or less, P: 0.025 mass% or less, S: 0.025 mass% or less and O: 0.0015 mass% or less, A value according to the following (1) is 770 or more and 850 or less, B value according to the following formula (2) is 0.40 or more, and the balance of inevitable impurities and Fe Steel for reinforcing steel with component composition.
- the component composition further comprises: Al: 0.50 mass% or less, 2.
- the component composition further includes: W: 2.0 mass% or less, Nb: 0.1% by mass or less, The steel for reinforcing steel as described in 1 or 2 above, containing one or more selected from Ti: 0.2% by mass or less and V: 0.5% by mass or less.
- the component composition further includes: B: The steel for reinforcing steel as described in any one of 1 to 3 above, containing 0.005% by mass or less.
- reinforcing bars that has excellent wire drawing properties and can manufacture high-strength reinforcing bars.
- Reinforcing bars using this steel for reinforcing steel, or reinforcing steel manufactured by drawing and heat treatment from steel for reinforcing steel have a tensile strength of 1600 MPa or more and excellent bending workability. It greatly contributes to slim, light weight and high-rise, and brings about an industrially beneficial effect.
- C 0.37% by mass or more and 0.50% by mass or less
- C is an essential element for ensuring the necessary strength, and if it is less than 0.37% by mass, it is difficult to ensure the predetermined strength, and in order to ensure the predetermined strength, an alloy It is necessary to add a large amount of element, which causes an increase in alloy cost.
- addition exceeding 0.50% by mass significantly increases the strength, which in turn increases the strength of the reinforcing bar more than necessary, leading to a decrease in bending workability. More preferably, it is in the range of 0.37 to 0.45 mass%.
- Si 1.75 mass% or more and 2.30 mass% or less Si is an element that increases the strength of steel by improving solid solution strengthening and temper softening resistance as a deoxidizer, and also a ferrite decarburization promoting element. As will be described later, it is also useful for securing a surface layer region of HV250 or less. Therefore, in this invention, it adds at 1.75 mass% or more. However, addition exceeding 2.30% by mass lowers the ductility and causes cracks in the material during casting, necessitating care of the material, leading to an increase in manufacturing costs. Therefore, the upper limit of Si is 2.30% by mass. More preferably, it is in the range of 1.75 to 2.25% by mass.
- Mn 0.2 mass% or more and 1.0 mass% or less Mn is added at 0.2 mass% or more in order to improve the hardenability of the steel.
- the upper limit of Mn is 1.0% by mass. More preferably, it is in the range of 0.25 to 1.0% by mass.
- Cr 0.01% by mass or more and 1.20% by mass or less Cr is an element that improves the hardenability of the steel and increases the strength. Therefore, 0.01 mass% or more is added. On the other hand, addition exceeding 1.20% by mass increases the strength of the steel on the contrary, which leads to a reduction in the wire drawability during drawing and the bending workability as a high strength rebar. From the above, the Cr content is set to 0.01% by mass or more and 1.20% by mass or less. More preferably, it is in the range of 0.01 to 1.00% by mass.
- Mo 0.05 mass% or more and 1.0 mass% or less Mo is an element that improves the hardenability of the steel and increases the strength. Therefore, 0.05 mass% or more is added. On the other hand, addition exceeding 1.0% by mass increases the strength of the steel on the contrary, so that the drawability at the time of drawing and the bending workability as a high-strength reinforcing bar are reduced. From the above, the amount of Mo is set to 0.05% by mass or more and 1.0% by mass or less. More preferably, it is in the range of 0.05 to 0.5% by mass.
- S 0.025% by mass or less
- P and S are segregated at grain boundaries to cause a reduction in the base metal toughness of the steel.
- S since S is present in steel as MnS, MnS may be the starting point during bending, and cracks are likely to occur. Therefore, it is necessary to suppress as much as possible. Is preferred.
- P and S since it will require high cost to make P and S each less than 0.0002 mass%, it is preferable industrially that P and S contain 0.0002 mass% or more, respectively.
- O 0.0015% by mass or less
- O is bonded to Si or Al to form hard oxide-based non-metallic inclusions, which may be the starting point during bending and may easily crack.
- up to 0.0015% by mass is allowed.
- O since it will require high cost to make O less than 0.0005 mass%, it is preferable industrially that O is contained 0.0005 mass% or more.
- a value (the above formula (1)): 770 or more and 850 or less
- the A value is an index for obtaining good strength, drawability and bending workability. If the A value is less than 770, the bending workability is good, but it is difficult to ensure the strength of the reinforcing bars. On the other hand, when the A value exceeds 850, good strength can be obtained, but the hardness of the steel for reinforcing bars is increased, causing breakage at the time of drawing, and the drawability is lowered. Furthermore, since the bending workability as a reinforcing bar is lowered, the A value is set to 770 or more and 850 or less in the present invention. More preferably, it is the range of 770 or more and 849 or less.
- the B value (the above formula (2)): 0.40 or more
- the B value is an index for obtaining good wire drawing.
- the reason why the drawability and bending workability are improved by setting the B value to 0.40 or more is that a decarburized layer is formed in the surface layer region of the steel for reinforcing bars or the surface layer region of the reinforcing bars, and the hardness of this surface layer region is This is because the processability is lowered and the processability is improved.
- the hardness in the thickness region of at least 20 ⁇ m or more from the surface becomes HV250 or less, and the drawability Can be good. Further, by setting the B value to 0.40 or more, the hardness of the region having a thickness of at least 10 ⁇ m or more from the surface of the reinforcing bar can be made HV300 or less, and the bending workability can be improved.
- Table 1 shows the component composition
- Table 2 shows the evaluation results of the range of HV250 or less, the hardness, the tensile strength as the reinforcing bar, and the bending workability of the reinforcing steel.
- the manufacturing conditions are as follows. First, the steel ingot melted by vacuum melting was heated from room temperature to the heating temperature shown in Table 2 at the heating rate shown in Table 2, and then hot rolled. The manufacturing conditions after hot rolling were the same. That is, after hot rolling was completed at 850 ° C., it was cooled at 1 ° C./s to obtain a wire having a diameter of 13.5 mm, which was used as a steel for reinforcing steel. The hardness of the cross section perpendicular to the longitudinal direction of the obtained wire was measured. The hardness was measured by the test method described later.
- a reinforcing bar was manufactured.
- the manufacturing conditions for the reinforcing bars were the same. That is, the manufacturing conditions are as follows. A 13.5 mm wire was drawn to 12.6 mm, and then quenched and tempered by heating to 1000 ° C., cooling with 60 ° C. oil, heating to 350 ° C., and water cooling. The drawability was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
- the wire rod after quenching and tempering was processed into a tensile test piece having a parallel portion of 1/4 in. Described in ASTM E8. The bending workability was tested by the test method described later after cutting to 500 mm length.
- Table 2 shows the range of steel for reinforcing steels in the range of HV250 or less, the hardness in the depth region (1 / 4D part) from the surface of the wire diameter D, the drawability at the time of drawing, the tensile strength as a reinforcing bar, Bending workability was shown.
- Table 2 shows the range of steel for reinforcing steels in the range of HV250 or less, the hardness in the depth region (1 / 4D part) from the surface of the wire diameter D, the drawability at the time of drawing, the tensile strength as a reinforcing bar, Bending workability was shown.
- Table 2 shows the range of steel for reinforcing steels in the range of HV250 or less, the hardness in the depth region (1 / 4D part) from the surface of the wire diameter D, the drawability at the time of drawing, the tensile strength as a reinforcing bar, Bending workability was shown.
- the A value and the B value are controlled within the range of the
- the manufacturing conditions of the reinforcing bars were the same. That is, the manufacturing conditions are as follows. First, a steel ingot melted by vacuum melting was heated to 1100 ° C. and then hot forged into a round bar having a diameter of 11.5 mm. The obtained round bar was processed into a tensile test piece having a parallel part of 1/4 in. Described in ASTM E8 and subjected to quenching and tempering treatment. Table 4 shows the heating temperature and holding time of the quenching treatment, and the tempering temperature and holding time of the tempering treatment. For bending workability, the round bar after hot forging was cut into a length of 500 mm, and then quenched and tempered under the above-described conditions, and the test was performed by the test method described later.
- Table 4 shows the evaluation results of tensile strength, range of HV300 or less, and bending workability. As shown in this table, when both the A value and the B value are controlled within the range of the present invention, it can be seen that good tensile strength, a range of HV300 or less and bending workability can be obtained. From the above, it was found that by adjusting the A value to 770 or more and 850 or less and the B value to 0.40 or more, the bending workability is improved while the strength is increased when the reinforcing bar is used.
- the hardness of the steel at least 20 ⁇ m from the surface in the steel for reinforcing bars is HV250 or less, and from the surface to the steel material
- the hardness of the depth region (1 / 4D part) of 1/4 of the diameter is HRC40 or less, and the hardness of the thickness region at least 10 ⁇ m from the surface after quenching and tempering is HV300 or less. Recognize. Note that the hardness of the surface layer is preferably regulated as described above. The reason for this is as follows.
- the hardness of the thickness region of at least 20 ⁇ m from the surface is HV250 or less
- the reason why the hardness of the thickness region of at least 20 ⁇ m from the surface is preferably HV250 or less is that if the hardness of this region exceeds HV250, high strength steel for rebar This is because the hardness of the wire becomes high and the drawability is lowered, and the wire breakage tends to occur during the drawing process.
- the reason why the thickness is in the range of at least 20 ⁇ m from the surface is that when the thickness is less than 20 ⁇ m, the high ductility region from the surface becomes small, and on the contrary, the strands are easily broken during the drawing process.
- the region expands to a depth of more than 100 ⁇ m from the surface, the strength as a high-strength reinforcing bar will decrease, so that the overall strength of the core will be further increased to achieve a tensile strength of 1600 MPa or more.
- the drawability at the time of drawing and the bending workability as a high-strength reinforcing bar tend to be lowered. Therefore, the region below HV250 is sufficient up to a depth of 100 ⁇ m from the surface.
- the steel is heated in the atmosphere to Ac 3 point or more at a heating rate of 30 ° C./min or less. This step can be performed in a raw material heating step for hot rolling described later.
- Hardness in the depth region of 1/4 of the steel diameter from the surface is HRC40 or less
- the reason why the hardness in the depth region of 1/4 of the steel diameter from the surface is preferably HRC40 or less is that this region is HRC40 If the temperature is too high, the region subjected to the processing during the drawing process becomes hard, the die life is shortened, and the material is easily broken.
- the 1/4 depth region refers to a portion (1 / 4D portion) whose distance from the steel surface is 1/4 of the diameter D of the steel material.
- a steel wire rod for rebar is manufactured by hot rolling, The rolling is preferably finished at Ar 3 points or more, and then the cooling rate to at least 700 ° C. is preferably 2 ° C./s or less.
- the hardness of the rebar after quenching and tempering is HV300 or less in the thickness area of at least 10 ⁇ m from the surface.
- the reason why the hardness of the thickness area of at least 10 ⁇ m from the surface is preferably HV300 or less is that the hardness in this area exceeds HV300 When it becomes, since hardness will become high and ductility will fall, it will become easy to produce a crack in a reinforcing steel surface layer at the time of bending. Therefore, in the present invention, the hardness of the surface layer region is preferably HV300 or less.
- the reason why the surface layer region is set to a range from the surface to a depth of at least 10 ⁇ m is that when the thickness is less than 10 ⁇ m, the high ductility region becomes small, and cracks tend to occur in the reinforcing steel surface layer during bending. From the above, it is preferable that the hardness of the thickness region of at least 10 ⁇ m from the surface is HV300 or less.
- HV300 the hardness of the thickness region of at least 10 ⁇ m from the surface.
- the region to be HV300 or less is 10 ⁇ m to 150 ⁇ m in depth from the surface. That is, when the depth region from the surface to be HV300 or less exceeds 150 ⁇ m, the strength of the reinforcing bar is decreased, and therefore the depth from the surface to the region to be HV300 or less is preferably 150 ⁇ m or less. Further, the region of HV300 or less is preferably a ferrite single phase structure. This is because stress concentration occurs in the surface layer during bending, but if the region below HV300 is a ferrite single-phase structure, stress concentration is relaxed by the high ductility of ferrite and bending workability is improved.
- the bainite structure also has a certain degree of ductility, it may be mixed in the structure within a range that can satisfy HV300 or less.
- the core structure of the reinforcing bar is preferably a martensite structure in order to ensure the strength as a reinforcing bar.
- the steel for reinforcing bars of the present invention can contain the following components in addition to the above components in order to increase the strength and improve the bending workability of the reinforcing bars.
- Cu and Ni are elements that increase hardenability and strength after tempering, and are selected. Can be added.
- Cu and Ni are preferably added at 0.005 mass% or more. However, if Cu is added in an amount of 1.0% by mass and Ni is added in an amount exceeding 2.0% by mass, the alloy cost is increased. Therefore, it is preferable to add Cu at an upper limit of 1.0% by mass and Ni at an upper limit of 2.0% by mass.
- Al is useful as a deoxidizer, and is an element effective for maintaining strength by suppressing the growth of austenite grains during quenching. Therefore, Al is preferably added in an amount of 0.01% by mass or more. However, even if added over 0.50% by mass, the effect is saturated, resulting in a disadvantage incurring a cost increase, and the oxide in the steel is increased, which becomes a starting point during bending and the bending workability is lowered. Therefore, Al is preferably added with an upper limit of 0.50% by mass.
- W 2.0% by mass or less
- Nb 0.1% by mass or less
- Ti 0.2% by mass or less
- V 0.5% by mass or less
- W, Nb, Ti and V are all hardenable It is an element that enhances the strength of steel after tempering, and can be selected and added according to the required strength. In order to obtain such an effect, it is preferable to add 0.001% by mass or more for W, Nb, and Ti and 0.002% by mass or more for V, respectively.
- Nb is added in an amount of more than 0.1% by mass
- Ti is added in an amount of more than 0.2% by mass
- a large amount of hard carbide / nitride / carbonitride is generated in the steel, and cracking occurs during bending. It tends to be a starting point and causes a decrease in bending workability.
- Nb, Ti and V are preferably added with the above values as upper limits.
- W is added in excess of 2.0% by mass, the wire drawing property and bending workability are lowered due to the increase in strength, and the alloy cost is increased. Therefore, it is preferable to add W with an upper limit of 2.0% by mass.
- B 0.005% by mass or less
- B is an element that increases the strength of the steel after tempering by increasing hardenability, and can be contained as necessary. In order to acquire the said effect, adding at 0.0002 mass% or more is preferable. However, when it exceeds 0.005 mass%, bending workability will deteriorate. Therefore, B is preferably added in the range of 0.0002 to 0.005 mass%.
- the steel ingot having the above component composition can be used either by melting by a converter or by vacuum melting. And steel ingots, slabs, blooms, billets and other materials are heated and hot rolled, pickled and scaled, drawn, adjusted to a predetermined thickness, heat treated, and rebar Used for industrial steel.
- the reinforcing bars manufactured using the steel for reinforcing bars of the present invention preferably have the above component composition and have a tensile strength of 1600 MPa or more. In other words, if the tensile strength is less than 1600 MPa, it is not possible to cope with the increase in the concrete strength of the rebar, so 1600 MPa or more is necessary.
- the steel for reinforcing bars from which the scale has been removed is then drawn and adjusted to a predetermined thickness in the atmosphere. It is preferable to heat to Ac 3 point or higher and quench (cooling rate is 60 ° C./s or higher), and then temper in a temperature range of 100 to 600 ° C. That is, the tempering temperature is preferably 100 ° C. or higher from the viewpoint of ensuring bending workability, and preferably 600 ° C. or lower from the viewpoint of ensuring a tensile strength of 1600 MPa or higher.
- the rebar manufactured through the above manufacturing process has a tempered martensite at the core.
- the surface layer portion has a decarburized layer, and further, decarburization is promoted by quenching and tempering, so that the surface layer portion has lower hardness than the core portion. That is, in the metal structure in the reinforcing bar of the present invention, the surface layer region described above is a ferrite single phase structure or a mixed structure of ferrite and bainite, and the structure inside the radial direction is tempered martensite. As a result, a high-strength reinforcing bar having excellent bending workability is obtained.
- the reinforcing bars thus obtained can be manufactured at low cost, they have excellent bending workability despite their high strength, and are applicable to shear reinforcements such as high-rise apartment buildings that require high strength of 1600 MPa or more. Is possible.
- the obtained wire was drawn to 12.6 mm, then heated to 1000 ° C. in the atmosphere and held for 300 seconds to obtain an oil at 60 ° C. After cooling at 350 ° C., it was maintained for 30 seconds after being heated at 350 ° C., and then water-cooled and quenched and tempered.
- the wire drawability as a steel material for reinforcing bars was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
- the wire rod after quenching and tempering is processed into a tensile test piece having a parallel part of 1/4 in.
- the bending test piece was obtained by cutting a wire having a diameter D of 11.5 mm into a length of 500 mm, and then performing quenching and tempering under the above-described heat treatment conditions.
- the drawability was evaluated by the presence or absence of wire breakage when a steel for reinforcing steel with a diameter of 13.5 mm was drawn to 12.6 mm.
- the number of wire breaks indicates the number of wire breaks during the 200 m drawing process, and it was judged that the wire drawability was lowered when the wire breakage occurred even once.
- Table 6 shows the range of HV250 and below, the structure of the steel for reinforcing bars, the structure and hardness of the 1 / 4D part, the drawability at the time of drawing, and the wire rod after the drawing was prepared by quenching and tempering.
- tissue, tensile strength, and bending workability is shown.
- Steels of C-1 to 4, C-6 to 10, C-16 to 19, and C-22 to 24 that satisfy the component composition, A value, and B value of the present invention have good drawability at the time of drawing, It can be seen that the tensile strength and bending workability are good.
- the C-5 steel whose B value does not satisfy the range of the present invention cannot satisfy the range of the present invention because the range of HV250 or less does not satisfy the range of the present invention. It can be seen that the sex has decreased.
- C-11-15, C-20-21, and C-25-26 steels whose component composition does not meet the scope of the present invention are drawn at the time of drawing, tensile strength at high strength rebar, bending It can be seen that one of the sexes has declined.
- the wire D having a diameter D of 13.5 mm was manufactured by cooling at a cooling rate of at least 700 ° C. as shown in Table 8 at 2 ° C./s or less.
- the obtained wire was drawn to 11.5 mm, and then Ac 3 points or higher and 1200 ° C or lower in the atmosphere according to the conditions shown in Table 8 After heating to a temperature range of 60 ° C., cooling in oil at 60 ° C., heating and holding at a temperature range of 100 ° C. to 600 ° C., cooling with water and quenching and tempering were performed. The drawability was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
- the wire rod after quenching and tempering was processed into a tensile test piece having a parallel portion of 1/4 in. Described in ASTM E8, and the test was performed in the same manner as in Example 1 described above.
- Table 8 shows the steel for reinforcing steel, the range of HV250 or less and its structure, the structure and hardness of the 1 / 4D part, the drawability at the time of drawing, and the wire rod after the drawing was prepared by quenching and tempering.
- tissue, tensile strength, and bending workability is shown.
- Steels of D-1 to 4, D-6 to 10, D-16 to 19, and D-22 to 24 that satisfy the component composition of the present invention and the A value and the B value have good bending workability. I understand.
- the D-5 steel whose B value does not satisfy the range of the present invention has a low range of HV300 or less, resulting in a decrease in bending workability.
- steels of D-11 to 15, D-20 to 21, and D-25 to 26 whose component composition does not meet the scope of the present invention are reduced in tensile strength, range of HV300 or less, or bending workability. You can see that
Abstract
Description
まず、特許文献1には、C、Si、Mnを適正範囲に制御し、冷却条件を制御することによって、表面のフェライト脱炭を0.12mm以上確保する、熱処理方法が開示されている。しかしながら、フェライト脱炭が0.12mm以上になると、高強度鉄筋を製造した場合の強度確保が困難となるため、フェライト脱炭層以外を高強度化する必要があり、合金添加が必要となる。そのため、鉄筋用の素材の硬度が上昇し、伸線性の低下を招くことになる。また、高強度鉄筋を製造後に、鉄筋の靭性が低下し、曲げ加工性が低下する。また、フェライト脱炭層を0.12mm以上にするには、添加するSi量にもよるが、830~900℃の温度範囲を少なくとも30秒超間保持することが必要であり、600~700℃の温度範囲に1時間以上保持することが好ましいことから、操業時の能率が低下し、余分な操業コストがかかる。 Thus, several proposals have been made to overcome the above problems.
First, Patent Document 1 discloses a heat treatment method in which C, Si, and Mn are controlled within an appropriate range, and cooling conditions are controlled to ensure a surface decarburization of 0.12 mm or more. However, when the ferrite decarburization is 0.12 mm or more, it is difficult to ensure the strength when a high-strength reinforcing bar is manufactured. Therefore, it is necessary to increase the strength other than the ferrite decarburized layer, and it is necessary to add an alloy. Therefore, the hardness of the material for reinforcing bars is increased, and the drawability is lowered. Moreover, after manufacturing a high-strength reinforcing bar, the toughness of the reinforcing bar is lowered and the bending workability is lowered. Further, in order to make the ferrite decarburized layer 0.12 mm or more, it is necessary to maintain a temperature range of 830 to 900 ° C. for at least 30 seconds, depending on the amount of Si to be added, and a temperature of 600 to 700 ° C. Since it is preferable to hold in the range for 1 hour or more, the efficiency at the time of operation falls, and an extra operation cost starts.
その結果、C、Si、Mn、CrおよびMoの添加量を適正化することに加えて、C、SiおよびCrについては所定の関係の下に添加量を規制することが、良好な伸線性を確保しつつ、高強度でありながら良好な曲げ加工性を有する鉄筋またはその素材となり得る、鉄筋用鋼の提供に不可欠であることを見出し、本発明を完成するに至った。 In order to solve the above-mentioned problems, the inventors manufactured high-strength steel for reinforcing bars with various amounts of addition of C, Si, Mn, Cr and Mo, and made the wire drawing property and hardness of the steel for reinforcing steel (drawing). Hard investigation of the hardness of the previous material. The steel for high-strength reinforcing steel was drawn and subjected to heat treatment, and the tensile strength and bending workability of the high-strength reinforcing steel produced by conducting heat treatment were intensively investigated.
As a result, in addition to optimizing the amount of addition of C, Si, Mn, Cr and Mo, it is possible to regulate the amount of addition of C, Si and Cr under a predetermined relationship. It has been found that it is indispensable for the provision of steel for reinforcing bars that can be used as a reinforcing bar or a material thereof having high bending strength while ensuring high strength, and has completed the present invention.
1.C:0.37質量%以上0.50質量%以下、
Si:1.75質量%以上2.30質量%以下、
Mn:0.2質量%以上1.0質量%以下、
Cr:0.01質量%以上1.2質量%以下
Mo:0.05質量%以上1.0質量%以下、
P:0.025質量%以下、
S:0.025質量%以下および
O:0.0015質量%以下
を含み、下記(1)に従うA値が770以上850以下、下記(2)式に従うB値が0.40以上であり、残部不可避的不純物およびFeの成分組成を有する鉄筋用鋼。
記
A=α+β+γ ・・・(1)
ここで、α=-334×[C]2+806×[C]+291
β=24×[Si]2+67×[Si]
γ=-4×[Cr]2+23×[Cr]-5
B=[Si]/[10×C] ・・・(2)
但し、上記の[ ]は、該括弧内成分の含有量(質量%) That is, the gist configuration of the present invention is as follows.
1. C: 0.37 mass% or more and 0.50 mass% or less,
Si: 1.75% by mass to 2.30% by mass,
Mn: 0.2% by mass or more and 1.0% by mass or less,
Cr: 0.01% by mass or more and 1.2% by mass or less Mo: 0.05% by mass or more and 1.0% by mass or less,
P: 0.025 mass% or less,
S: 0.025 mass% or less and O: 0.0015 mass% or less, A value according to the following (1) is 770 or more and 850 or less, B value according to the following formula (2) is 0.40 or more, and the balance of inevitable impurities and Fe Steel for reinforcing steel with component composition.
A = α + β + γ (1)
Here, α = −334 × [C] 2 + 806 × [C] +291
β = 24 × [Si] 2 + 67 × [Si]
γ = −4 × [Cr] 2 + 23 × [Cr] −5
B = [Si] / [10 × C] (2)
However, the above [] is the content (mass%) of the component in parentheses.
Al:0.50質量%以下、
Cu:1.0質量%以下および
Ni:2.0質量%以下
のうちから選ばれる1種または2種以上を含有する前記1に記載の鉄筋用鋼。 2. The component composition further comprises:
Al: 0.50 mass% or less,
2. The steel for reinforcing bars as described in 1 above, containing one or more selected from Cu: 1.0% by mass or less and Ni: 2.0% by mass or less.
W:2.0質量%以下、
Nb:0.1質量%以下、
Ti:0.2質量%以下および
V:0.5質量%以下
のうちから選ばれる1種または2種以上を含有する前記1または2に記載の鉄筋用鋼。 3. The component composition further includes:
W: 2.0 mass% or less,
Nb: 0.1% by mass or less,
The steel for reinforcing steel as described in 1 or 2 above, containing one or more selected from Ti: 0.2% by mass or less and V: 0.5% by mass or less.
B:0.005質量%以下
を含有することを特徴とする前記1ないし3のいずれかに記載の鉄筋用鋼。 4). The component composition further includes:
B: The steel for reinforcing steel as described in any one of 1 to 3 above, containing 0.005% by mass or less.
C:0.37質量%以上0.50質量%以下
Cは、必要な強度を確保するために必須の元素であり、0.37質量%未満では所定の強度確保が難しく、また所定強度を確保するためには、合金元素の多量添加が必要となって、合金コストの上昇を招くことから、0.37質量%以上とする。一方、0.50質量%を超える添加は、強度を大幅に上昇して、ひいては鉄筋の必要以上の強度上昇を招いて曲げ加工性の低下を招くことから、0.50質量%以下とする。より好ましくは、0.37~0.45質量%の範囲である。 Next, the component composition of the reinforcing bar of the present invention and the production conditions will be described.
C: 0.37% by mass or more and 0.50% by mass or less C is an essential element for ensuring the necessary strength, and if it is less than 0.37% by mass, it is difficult to ensure the predetermined strength, and in order to ensure the predetermined strength, an alloy It is necessary to add a large amount of element, which causes an increase in alloy cost. On the other hand, addition exceeding 0.50% by mass significantly increases the strength, which in turn increases the strength of the reinforcing bar more than necessary, leading to a decrease in bending workability. More preferably, it is in the range of 0.37 to 0.45 mass%.
Siは、脱酸剤として、また固溶強化や焼戻し軟化抵抗を向上させることにより鋼の強度を高める元素であり、またフェライト脱炭促進元素であるため、後述するようにHV250以下となる表層領域を確保する上でも有用である。よって、本発明では、1.75質量%以上で添加する。しかし、2.30質量%を超える添加は、延性が低下し、鋳造時に素材に割れが発生するため、素材の手入れが必要となり製造コストの増加を招く。よって、Siの上限は2.30質量%とする。より好ましくは、1.75 ~2.25質量%の範囲である。 Si: 1.75 mass% or more and 2.30 mass% or less Si is an element that increases the strength of steel by improving solid solution strengthening and temper softening resistance as a deoxidizer, and also a ferrite decarburization promoting element. As will be described later, it is also useful for securing a surface layer region of HV250 or less. Therefore, in this invention, it adds at 1.75 mass% or more. However, addition exceeding 2.30% by mass lowers the ductility and causes cracks in the material during casting, necessitating care of the material, leading to an increase in manufacturing costs. Therefore, the upper limit of Si is 2.30% by mass. More preferably, it is in the range of 1.75 to 2.25% by mass.
Mnは、鋼の焼入れ性を向上させるため、0.2質量%以上で添加する。しかし、1.0質量%を超える添加は、却って鋼の強度を低下させる。よって、Mnの上限は、1.0質量%とする。より好ましくは、0.25 ~1.0質量%の範囲である。 Mn: 0.2 mass% or more and 1.0 mass% or less Mn is added at 0.2 mass% or more in order to improve the hardenability of the steel. However, addition exceeding 1.0% by mass reduces the strength of the steel. Therefore, the upper limit of Mn is 1.0% by mass. More preferably, it is in the range of 0.25 to 1.0% by mass.
Crは、鋼の焼入れ性を向上させ強度を増加させる元素である。そのため、0.01質量%以上は添加する。一方、1.20質量%を超えての添加は、却って鋼を高強度化するため、引抜加工時の伸線性、高強度鉄筋としての曲げ加工性の低下を招く。以上のことから、Cr量は0.01質量%以上1.20質量%以下とする。より好ましくは、0.01~1.00質量%の範囲である。 Cr: 0.01% by mass or more and 1.20% by mass or less Cr is an element that improves the hardenability of the steel and increases the strength. Therefore, 0.01 mass% or more is added. On the other hand, addition exceeding 1.20% by mass increases the strength of the steel on the contrary, which leads to a reduction in the wire drawability during drawing and the bending workability as a high strength rebar. From the above, the Cr content is set to 0.01% by mass or more and 1.20% by mass or less. More preferably, it is in the range of 0.01 to 1.00% by mass.
Moは、鋼の焼入れ性を向上させ強度を増加させる元素である。そのため、0.05質量%以上は添加する。一方、1.0質量%を超えての添加は、却って鋼を高強度化するため、引抜加工時の伸線性、高強度鉄筋としての曲げ加工性の低下を招く。以上のことから、Mo量は0.05質量%以上1.0質量%以下とする。より好ましくは、0.05~0.5質量%の範囲である。 Mo: 0.05 mass% or more and 1.0 mass% or less Mo is an element that improves the hardenability of the steel and increases the strength. Therefore, 0.05 mass% or more is added. On the other hand, addition exceeding 1.0% by mass increases the strength of the steel on the contrary, so that the drawability at the time of drawing and the bending workability as a high-strength reinforcing bar are reduced. From the above, the amount of Mo is set to 0.05% by mass or more and 1.0% by mass or less. More preferably, it is in the range of 0.05 to 0.5% by mass.
S:0.025質量%以下
PおよびSは、粒界に偏析して鋼の母材靭性の低下を招くことから、それぞれ0.025質量%以下に規制する。とくに、SはMnSとして鋼中に存在するため、曲げ加工時にMnSが起点となり亀裂が生じ易くなる可能性があるため、極力抑制する必要があり、可能であれば、0.015質量%以下とすることが好ましい。なお、PおよびSをそれぞれ0.0002質量%未満とすることは高いコストを要することから、工業的にはPおよびSはそれぞれ0.0002質量%以上含有されていることが好ましい。 P: 0.025% by mass or less S: 0.025% by mass or less P and S are segregated at grain boundaries to cause a reduction in the base metal toughness of the steel. In particular, since S is present in steel as MnS, MnS may be the starting point during bending, and cracks are likely to occur. Therefore, it is necessary to suppress as much as possible. Is preferred. In addition, since it will require high cost to make P and S each less than 0.0002 mass%, it is preferable industrially that P and S contain 0.0002 mass% or more, respectively.
Oは、SiやAlと結合し、硬質な酸化物系非金属介在物を形成し、曲げ加工時に起点となり亀裂が生じ易くなる可能性があるため、可能な限り低い方が良いが、本発明では、0.0015質量%までは許容される。なお、Oを0.0005質量%未満とすることは高いコストを要することから、工業的にはOは0.0005質量%以上含有されていることが好ましい。 O: 0.0015% by mass or less O is bonded to Si or Al to form hard oxide-based non-metallic inclusions, which may be the starting point during bending and may easily crack. However, in the present invention, up to 0.0015% by mass is allowed. In addition, since it will require high cost to make O less than 0.0005 mass%, it is preferable industrially that O is contained 0.0005 mass% or more.
A値は、良好な強度、伸線性ならびに曲げ加工性を得るための指数である。このA値が770未満であると、曲げ加工性は良好であるが、鉄筋の強度確保が困難となる。一方、A値が850を超えると、良好な強度を得ることはできるが、鉄筋用鋼の硬度が上昇して引き抜き加工時に断線を招くことになり、却って伸線性が低下する。さらには、鉄筋としての曲げ加工性が低下するため、本発明では、A値を770以上850以下とする。より好ましくは、770以上849以下の範囲である。 A value (the above formula (1)): 770 or more and 850 or less The A value is an index for obtaining good strength, drawability and bending workability. If the A value is less than 770, the bending workability is good, but it is difficult to ensure the strength of the reinforcing bars. On the other hand, when the A value exceeds 850, good strength can be obtained, but the hardness of the steel for reinforcing bars is increased, causing breakage at the time of drawing, and the drawability is lowered. Furthermore, since the bending workability as a reinforcing bar is lowered, the A value is set to 770 or more and 850 or less in the present invention. More preferably, it is the range of 770 or more and 849 or less.
B値は、良好な伸線性を得るための指数である。このB値を0.40以上とすることによって、鉄筋用鋼においては良好な伸線性を、鉄筋においては良好な曲げ加工性を確保することができる。なお、B値を0.40以上にすることにより、伸線性や曲げ加工性が良好となる理由は、鉄筋用鋼の表層域あるいは鉄筋の表層域に脱炭層が形成し、この表層域の硬さが低下して加工性が良好となるためである。具体的には、後述する実験結果で詳細は説明するように、B値を0.40以上とすることで、鉄筋用鋼においては表面から少なくとも20μm以上の厚み領域の硬さがHV250以下となり、伸線性を良好とすることができる。また、B値を0.40以上とすることにより、鉄筋においては表面から少なくとも10μm以上の厚みの領域の硬さをHV300以下とすることができ、曲げ加工性を良好とすることができる。 B value (the above formula (2)): 0.40 or more The B value is an index for obtaining good wire drawing. By setting this B value to 0.40 or more, it is possible to ensure good wire drawing in steel for reinforcing bars and good bending workability in reinforcing steel. The reason why the drawability and bending workability are improved by setting the B value to 0.40 or more is that a decarburized layer is formed in the surface layer region of the steel for reinforcing bars or the surface layer region of the reinforcing bars, and the hardness of this surface layer region is This is because the processability is lowered and the processability is improved. Specifically, as will be described in detail in the experimental results to be described later, by setting the B value to 0.40 or more, in the steel for reinforcing bars, the hardness in the thickness region of at least 20 μm or more from the surface becomes HV250 or less, and the drawability Can be good. Further, by setting the B value to 0.40 or more, the hardness of the region having a thickness of at least 10 μm or more from the surface of the reinforcing bar can be made HV300 or less, and the bending workability can be improved.
[実験1]
上記のA値およびB値について、発明者らは、成分組成とA値およびB値とを変化させた鉄筋用鋼を作製し、その硬度を調査した。さらには、この鉄筋用鋼に対して、引抜加工、焼入れ-焼戻し処理を行うことで鉄筋を製造し、引抜加工時の伸線性を調査するとともに、得られた鉄筋については、その引張強さ、表層硬さおよび曲げ加工性、さらには組織を調査した。なお、引張強さ、表層硬さおよび曲げ加工性は、後述する試験方法で測定を行った。表1に成分組成を、表2に鉄筋用鋼でのHV250以下の範囲、硬度と鉄筋としての引張強さ、曲げ加工性の評価結果を、それぞれ示す。 The inventors evaluated the effects of the component composition of steel for reinforcing steel, particularly the above-described A value and B value, on the drawability and bending workability in various experiments. Two typical experimental results are described in detail below.
[Experiment 1]
With respect to the above A value and B value, the inventors made steel for reinforcing bars in which the component composition, the A value, and the B value were changed, and investigated the hardness thereof. Furthermore, the steel for reinforcing bars is manufactured by drawing, quenching and tempering, and the wire drawing property at the time of drawing is investigated, and the tensile strength, The surface hardness and bending workability as well as the structure were investigated. In addition, the tensile strength, surface layer hardness, and bending workability were measured by the test method mentioned later. Table 1 shows the component composition, and Table 2 shows the evaluation results of the range of HV250 or less, the hardness, the tensile strength as the reinforcing bar, and the bending workability of the reinforcing steel.
まず、真空溶解で溶製した鋼塊を室温から表2に示す加熱速度で表2に示す加熱温度まで加熱後、熱間圧延を行った。熱間圧延以降の製造条件は同じにした。すなわち、熱間圧延を850℃で終了後に1℃/sで冷却し、直径13.5mmの線材とし、これを鉄筋用鋼とした。得られた線材の長手方向に垂直な断面の硬度測定を行った。硬度測定は後述する試験方法で試験を実施した。 The manufacturing conditions are as follows.
First, the steel ingot melted by vacuum melting was heated from room temperature to the heating temperature shown in Table 2 at the heating rate shown in Table 2, and then hot rolled. The manufacturing conditions after hot rolling were the same. That is, after hot rolling was completed at 850 ° C., it was cooled at 1 ° C./s to obtain a wire having a diameter of 13.5 mm, which was used as a steel for reinforcing steel. The hardness of the cross section perpendicular to the longitudinal direction of the obtained wire was measured. The hardness was measured by the test method described later.
13.5mmの線材を、12.6mmに引抜加工を行い、その後、1000℃に加熱後60℃の油で冷却し、350℃に加熱後水冷する、焼入れ-焼戻し処理を行った。伸線性は、この引抜加工時に素線が断線したかどうかで判断し、断線しなければ良好な伸線性を有していると判断した。
焼入れ-焼戻し後の線材を、ASTM E8に記載の平行部1/4in.の引張試験片に加工した。なお、曲げ加工性は、500mm長さに切断後、後述する試験方法で試験を実施した。 Next, using this steel for reinforcing bars as a raw material, a reinforcing bar was manufactured. The manufacturing conditions for the reinforcing bars were the same. That is, the manufacturing conditions are as follows.
A 13.5 mm wire was drawn to 12.6 mm, and then quenched and tempered by heating to 1000 ° C., cooling with 60 ° C. oil, heating to 350 ° C., and water cooling. The drawability was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
The wire rod after quenching and tempering was processed into a tensile test piece having a parallel portion of 1/4 in. Described in ASTM E8. The bending workability was tested by the test method described later after cutting to 500 mm length.
上記のA値およびB値について、発明者らは、成分組成とA値およびB値とを変化させた鉄筋用鋼から鉄筋を作製し、その引張強さ、表層硬さおよび曲げ加工性、さらには組織を調査した。なお、引張強さ、表層硬さおよび曲げ加工性は、後述する試験方法に従って測定を行った。また、組織は、HV300以下の範囲における組織と、芯部(1/2D部:Dは鉄筋の直径)の組織を調査した。表3に成分組成を、表4に引張強さ、HV300以下の範囲および曲げ加工性の評価結果を、それぞれ示す。 [Experiment 2]
Regarding the above A value and B value, the inventors prepared reinforcing bars from steel for reinforcing bars in which the component composition and the A value and B value were changed, and the tensile strength, surface hardness and bending workability, Investigated the organization. In addition, the tensile strength, surface layer hardness, and bending workability were measured according to the test method mentioned later. Moreover, the structure | tissue in the range below HV300 and the structure | tissue of a core part (1 / 2D part: D is the diameter of a reinforcing bar) were investigated. Table 3 shows the component composition, and Table 4 shows the tensile strength, the range of HV300 or less, and the bending workability evaluation results.
まず、真空溶解で溶製した鋼塊を1100℃に加熱後、熱間鍛伸を行って直径11.5mmの丸棒にした。得られた丸棒を、ASTM E8に記載の平行部1/4in.の引張試験片に加工し、焼入れ-焼戻し処理を行った。このときの焼入れ処理の加熱温度、保持時間、および、焼戻し処理の焼戻し温度および保持時間は表4に示すとおりである。なお、曲げ加工性は、上述の熱間鍛伸後の丸棒を500mm長さに切断後、上述した条件で焼入れ-焼戻し処理を実施し、後述する試験方法で試験を実施した。 Here, in the evaluation, the manufacturing conditions of the reinforcing bars were the same. That is, the manufacturing conditions are as follows.
First, a steel ingot melted by vacuum melting was heated to 1100 ° C. and then hot forged into a round bar having a diameter of 11.5 mm. The obtained round bar was processed into a tensile test piece having a parallel part of 1/4 in. Described in ASTM E8 and subjected to quenching and tempering treatment. Table 4 shows the heating temperature and holding time of the quenching treatment, and the tempering temperature and holding time of the tempering treatment. For bending workability, the round bar after hot forging was cut into a length of 500 mm, and then quenched and tempered under the above-described conditions, and the test was performed by the test method described later.
表面から少なくとも20μmの厚み領域の硬さがHV250以下であることが好ましい理由は、この領域の硬さがHV250超えになると、高強度鉄筋用鋼の硬度が高くなり伸線性が低下し、引抜加工時に素線の断線が生じ易くなるからである。
また、表面から少なくとも20μmの厚みの範囲としたのは、同20μm未満になると表面からの高延性領域が小さくなり、却って引抜加工時に素線の断線が生じ易くなるからである。一方、該領域が表面から100μm超えの深さまでの領域に拡大すると、高強度鉄筋としての強度が低下するため、全体として引張強さを1600MPa以上とするためには芯部の更なる高強度化が必要となり、却って、引抜加工時の伸線性や、高強度鉄筋としての曲げ加工性が低下し易くなる。従って、HV250以下とする領域は、表面から100μmの深さまでで十分である。
ここで、表面から少なくとも20μmの厚み域の硬さをHV250以下とするには、鋼を大気中でAc3点以上に30℃/分以下の加熱速度で加熱することが好適である。この工程は、後述する熱間圧延のための素材加熱工程で行うことができる。 The hardness of the thickness region of at least 20μm from the surface is HV250 or less The reason why the hardness of the thickness region of at least 20μm from the surface is preferably HV250 or less is that if the hardness of this region exceeds HV250, high strength steel for rebar This is because the hardness of the wire becomes high and the drawability is lowered, and the wire breakage tends to occur during the drawing process.
Also, the reason why the thickness is in the range of at least 20 μm from the surface is that when the thickness is less than 20 μm, the high ductility region from the surface becomes small, and on the contrary, the strands are easily broken during the drawing process. On the other hand, if the region expands to a depth of more than 100 μm from the surface, the strength as a high-strength reinforcing bar will decrease, so that the overall strength of the core will be further increased to achieve a tensile strength of 1600 MPa or more. On the other hand, the drawability at the time of drawing and the bending workability as a high-strength reinforcing bar tend to be lowered. Therefore, the region below HV250 is sufficient up to a depth of 100 μm from the surface.
Here, in order to set the hardness in the thickness region of at least 20 μm from the surface to HV250 or less, it is preferable that the steel is heated in the atmosphere to Ac 3 point or more at a heating rate of 30 ° C./min or less. This step can be performed in a raw material heating step for hot rolling described later.
表面から鋼材の径の1/4の深さ域の硬さがHRC40以下であることが好ましい理由は、この領域がHRC40超となると、引抜加工時に加工を受ける領域が硬くなり、ダイスの寿命が短くなったり、素材の断線が生じやすくなるからである。ここで、1/4の深さ域とは、鋼材表面から距離が鋼材の径Dの1/4となる部分(1/4D部)のことである。 Hardness in the depth region of 1/4 of the steel diameter from the surface is HRC40 or less The reason why the hardness in the depth region of 1/4 of the steel diameter from the surface is preferably HRC40 or less is that this region is HRC40 If the temperature is too high, the region subjected to the processing during the drawing process becomes hard, the die life is shortened, and the material is easily broken. Here, the 1/4 depth region refers to a portion (1 / 4D portion) whose distance from the steel surface is 1/4 of the diameter D of the steel material.
表面から少なくとも10μmの厚み領域の硬さがHV300以下であることが好ましい理由は、この領域の硬さがHV300超えになると、硬度が高くなって延性が低下するため、曲げ加工時に鉄筋表層に割れが生じ易くなる。そのため、本発明では表層域の硬さがHV300以下であることが好ましい。また、表層域について表面から少なくとも10μmの深さまでの範囲としたのは、10μm未満になると高延性領域が小さくなり、曲げ加工時に鉄筋表層に割れが生じ易くなるためである。以上のことから、表面から少なくとも10μmの厚み領域の硬さがHV300以下であることが好ましい。
ここで、表面から10μm以上の厚み領域の硬さをHV300以下とするには、鋼を大気中でAc3点以上に加熱することが好適である。この工程は、後述する焼入れ工程で行うことができる。 The hardness of the rebar after quenching and tempering is HV300 or less in the thickness area of at least 10 μm from the surface. The reason why the hardness of the thickness area of at least 10 μm from the surface is preferably HV300 or less is that the hardness in this area exceeds HV300 When it becomes, since hardness will become high and ductility will fall, it will become easy to produce a crack in a reinforcing steel surface layer at the time of bending. Therefore, in the present invention, the hardness of the surface layer region is preferably HV300 or less. Further, the reason why the surface layer region is set to a range from the surface to a depth of at least 10 μm is that when the thickness is less than 10 μm, the high ductility region becomes small, and cracks tend to occur in the reinforcing steel surface layer during bending. From the above, it is preferable that the hardness of the thickness region of at least 10 μm from the surface is HV300 or less.
Here, in order to set the hardness in the thickness region of 10 μm or more from the surface to HV300 or less, it is preferable to heat the steel to Ac 3 points or more in the atmosphere. This step can be performed in a quenching step described later.
Al:0.50質量%以下、Cu:1.0質量%以下およびNi:2.0質量%以下のうちの1種または2種以上
CuおよびNiは、焼入れ性や焼戻し後の強度を高める元素であり、選択して添加することができる。このような効果を得るためには、CuおよびNiは0.005質量%以上で添加することが好ましい。しかし、Cuは1.0質量%およびNiは2.0質量%を超えて添加すると、却って合金コストが上昇するため、Cuは1.0質量%およびNiは2.0質量%を上限として添加するのが好ましい。
また、Alは脱酸剤として有用であり、さらに、焼入れ時のオーステナイト粒成長を抑制することによって、強度の維持に有効な元素であるため、好ましくは0.01質量%以上で添加する。しかしながら、0.50質量%を超えて添加しても、その効果は飽和してコスト上昇を招く不利が生じる上、鋼中の酸化物が増加し、曲げ加工時の起点となり曲げ加工性が低下する。よって、Alは0.50質量%を上限として添加することが好ましい。 Furthermore, the steel for reinforcing bars of the present invention can contain the following components in addition to the above components in order to increase the strength and improve the bending workability of the reinforcing bars.
One or more of Al: 0.50% by mass or less, Cu: 1.0% by mass or less, and Ni: 2.0% by mass or less Cu and Ni are elements that increase hardenability and strength after tempering, and are selected. Can be added. In order to obtain such an effect, Cu and Ni are preferably added at 0.005 mass% or more. However, if Cu is added in an amount of 1.0% by mass and Ni is added in an amount exceeding 2.0% by mass, the alloy cost is increased. Therefore, it is preferable to add Cu at an upper limit of 1.0% by mass and Ni at an upper limit of 2.0% by mass.
Further, Al is useful as a deoxidizer, and is an element effective for maintaining strength by suppressing the growth of austenite grains during quenching. Therefore, Al is preferably added in an amount of 0.01% by mass or more. However, even if added over 0.50% by mass, the effect is saturated, resulting in a disadvantage incurring a cost increase, and the oxide in the steel is increased, which becomes a starting point during bending and the bending workability is lowered. Therefore, Al is preferably added with an upper limit of 0.50% by mass.
W、Nb、TiおよびVは、いずれも焼入れ性や焼戻し後の鋼の強度を高める元素であり、必要とする強度に応じて選択して添加することができる。このような効果を得るためには、W、NbおよびTiは、それぞれ0.001質量%以上、Vは0.002質量%以上添加することが好ましい。しかし、Vは0.5質量%、Nbは0.1質量%およびTiは0.2質量%を超えて添加すると、鋼中に硬質な炭化物・窒化物・炭窒化物が多量に生成し、曲げ加工時に亀裂発生の起点となり易く、曲げ加工性の低下を招く。Nb、TiおよびVは、それぞれ上記の値を上限として添加するのが好ましい。また、Wは2.0質量%を超えて添加すると、高強度化による伸線性の低下や曲げ加工性の低下および、合金コストの上昇を招く。よって、Wは、2.0質量%を上限として添加するのが好ましい。 W: 2.0% by mass or less, Nb: 0.1% by mass or less, Ti: 0.2% by mass or less, and V: 0.5% by mass or less W, Nb, Ti and V are all hardenable It is an element that enhances the strength of steel after tempering, and can be selected and added according to the required strength. In order to obtain such an effect, it is preferable to add 0.001% by mass or more for W, Nb, and Ti and 0.002% by mass or more for V, respectively. However, when V is added in an amount of 0.5% by mass, Nb is added in an amount of more than 0.1% by mass and Ti is added in an amount of more than 0.2% by mass, a large amount of hard carbide / nitride / carbonitride is generated in the steel, and cracking occurs during bending. It tends to be a starting point and causes a decrease in bending workability. Nb, Ti and V are preferably added with the above values as upper limits. On the other hand, when W is added in excess of 2.0% by mass, the wire drawing property and bending workability are lowered due to the increase in strength, and the alloy cost is increased. Therefore, it is preferable to add W with an upper limit of 2.0% by mass.
Bは、焼入れ性の増大により焼戻し後の鋼の強度を高める元素であり、必要に応じて含有することができる。上記効果を得るためには、0.0002質量%以上で添加するのが好ましい。しかし、0.005質量%を超えて添加すると、曲げ加工性が劣化する。よって、Bは0.0002~0.005質量%の範囲で添加することが好ましい。 B: 0.005% by mass or less B is an element that increases the strength of the steel after tempering by increasing hardenability, and can be contained as necessary. In order to acquire the said effect, adding at 0.0002 mass% or more is preferable. However, when it exceeds 0.005 mass%, bending workability will deteriorate. Therefore, B is preferably added in the range of 0.0002 to 0.005 mass%.
さらに、焼入れ焼戻し後の線材に対して、ASTM E8に記載の平行部1/4in.の引張試験片に加工し、後述する試験方法で引張試験を実施するとともに、同試験片を用いて表層硬度と組織を調査した。また、曲げ試験片は、直径Dが11.5mmの線材を500mm長さに切断したのち、上述した熱処理条件での焼入れ焼戻しを行った。 Next, in order to evaluate the properties as a high-strength reinforcing bar, the obtained wire was drawn to 12.6 mm, then heated to 1000 ° C. in the atmosphere and held for 300 seconds to obtain an oil at 60 ° C. After cooling at 350 ° C., it was maintained for 30 seconds after being heated at 350 ° C., and then water-cooled and quenched and tempered. The wire drawability as a steel material for reinforcing bars was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
Furthermore, the wire rod after quenching and tempering is processed into a tensile test piece having a parallel part of 1/4 in. Described in ASTM E8, and a tensile test is performed by a test method described later, and the surface layer hardness is measured using the test piece. And investigated the organization. Further, the bending test piece was obtained by cutting a wire having a diameter D of 11.5 mm into a length of 500 mm, and then performing quenching and tempering under the above-described heat treatment conditions.
HV250以下の硬さの範囲の調査は、引抜加工前の線材(鉄筋用鋼)の先端、中間、尾端から直径が13.5mm、長さが5mmのサンプルを採取して行った。このサンプルを被検面が圧延方向に垂直な面(直径13.5mmの面)になるように埋め込み、鏡面研磨後、株式会社アカシ製微小硬さ試験機(HM-115)で荷重10gf、10μm深さピッチで測定を実施し、HV250以下となる領域を求めた。 [Surface hardness measurement]
The investigation of the hardness range below HV250 was conducted by collecting samples with a diameter of 13.5mm and a length of 5mm from the tip, middle and tail ends of the wire (steel for rebar) before drawing. This sample was embedded so that the test surface was a surface perpendicular to the rolling direction (diameter of 13.5 mm), mirror-polished, and then loaded with an Akashi micro hardness tester (HM-115) with a load of 10 gf and a depth of 10 μm. Measurement was carried out at a pitch, and the region where HV250 or less was obtained.
上述した表層硬度測定を行ったサンプルを用いて、1/4D部(Dは線材の直径)の硬度をミツトヨ製ロックウエル硬さ試験機(ARK-600)でCスケール、4点測定し平均を求めた。 [1 / 4D part hardness measurement]
Using the sample whose surface hardness was measured as described above, measure the hardness of 1 / 4D part (D is the diameter of the wire) on the C scale, 4 points with Mitutoyo Rockwell Hardness Tester (ARK-600) to obtain the average. It was.
上述した硬度測定を行ったサンプルを用いて、3%ナイタルで腐食後、HV250の範囲の組織、1/4D部の組織観察を行った。組織観察は500倍の倍率で観察を行った。 [Microstructure observation]
Using the samples subjected to the hardness measurement described above, the structure in the range of HV250 and the structure of the 1 / 4D part were observed after corrosion with 3% nital. Tissue observation was performed at a magnification of 500 times.
伸線性は、直径13.5mmの鉄筋用鋼を12.6mmに引抜加工を行うときの、断線の有無により評価した。断線回数は200m引抜加工時に断線した回数を示しており、断線が1回でも発生した場合に伸線性が低下したと判断した。 [Drawability]
The drawability was evaluated by the presence or absence of wire breakage when a steel for reinforcing steel with a diameter of 13.5 mm was drawn to 12.6 mm. The number of wire breaks indicates the number of wire breaks during the 200 m drawing process, and it was judged that the wire drawability was lowered when the wire breakage occurred even once.
鉄筋としての曲げ特性を調べるために、引抜加工、熱処理後の線材から、直径Dの4倍の曲げ直径(4D)で180°曲げを行い、曲げ加工性を評価した。曲げ加工後の線材に対して、浸透探傷試験を行って割れの有無を調査した。 [Bending test]
In order to investigate the bending characteristics as a reinforcing bar, the bending workability was evaluated by bending 180 ° with a bending diameter (4D) four times the diameter D from the wire after drawing and heat treatment. A penetration test was conducted on the wire after bending to investigate the presence of cracks.
高強度鉄筋としての引張特性を調べるために、引抜加工、熱処理後の線材から、ASTM E8に記載の平行部の直径1/4in.の引張試験片を採取して、評点間距離25.4mmおよび引張速度5mm/分にて試験を実施した。本発明では、引張強さが1600MPa以上であれば高強度鉄筋が得られたとして評価した。 [Tensile test]
In order to investigate the tensile properties of high-strength reinforcing bars, tensile test specimens with a diameter of 1/4 in. Of the parallel part described in ASTM E8 were collected from the wire after drawing and heat treatment. The test was carried out at a speed of 5 mm / min. In the present invention, it was evaluated that a high-strength reinforcing bar was obtained when the tensile strength was 1600 MPa or more.
HV300以下の範囲の調査は、上述した引張試験片で熱処理を実施し、平行部の中央部を切り出し、樹脂に埋め込み、鏡面研磨後、株式会社アカシ製の微小硬さ試験機(HM-115)を用いて、荷重10gfで表面から順に5μm深さピッチでの測定を実施し、HV300以下の領域を特定した。 [Measurement of surface hardness after quenching and tempering]
For the investigation of the range below HV300, heat treatment was performed with the above-mentioned tensile test piece, the central part of the parallel part was cut out, embedded in resin, mirror-polished, and a microhardness tester (HM-115) manufactured by Akashi Co., Ltd. , Measurement was performed at a 5 μm depth pitch in order from the surface with a load of 10 gf, and an area of HV300 or less was specified.
HV300以下の範囲における組織と、芯部(1/2D部:Dは線材の直径)の組織とを、それぞれ次のようにして観察した。すなわち、上述した硬度測定を行ったサンプルを用いて、3%ナイタルで腐食後、HV300以下の範囲の組織と、1/2D部の組織の組織観察を行った。組織観察は、500倍の倍率で行い、それぞれの位置における組織の同定を行った。 [Observation of structure after quenching and tempering]
The structure in the range of HV300 or less and the structure of the core part (1 / 2D part: D is the diameter of the wire) were observed as follows. That is, using the sample on which the hardness measurement described above was performed, after erosion with 3% nital, the structure in the range of HV300 or less and the structure of the 1 / 2D part structure were observed. Tissue observation was performed at a magnification of 500 times, and the tissue at each position was identified.
焼入れ焼戻し後の線材に対して、ASTM E8に記載の平行部1/4in.の引張試験片に加工し、上述の実施例1の場合と同様に試験を実施した。 Next, in order to evaluate the characteristics as a high-strength reinforcing bar, the obtained wire was drawn to 11.5 mm, and then Ac 3 points or higher and 1200 ° C or lower in the atmosphere according to the conditions shown in Table 8 After heating to a temperature range of 60 ° C., cooling in oil at 60 ° C., heating and holding at a temperature range of 100 ° C. to 600 ° C., cooling with water and quenching and tempering were performed. The drawability was judged by whether or not the wire was broken during the drawing process, and if it was not broken, it was judged that the wire had good drawability.
The wire rod after quenching and tempering was processed into a tensile test piece having a parallel portion of 1/4 in. Described in ASTM E8, and the test was performed in the same manner as in Example 1 described above.
Claims (6)
- C:0.37質量%以上0.50質量%以下、
Si:1.75質量%以上2.30質量%以下、
Mn:0.2質量%以上1.0質量%以下、
Cr:0.01質量%以上1.2質量%以下、
Mo:0.05質量%以上1.0質量%以下、
P:0.025質量%以下、
S:0.025質量%以下および
O:0.0015質量%以下
を含み、下記(1)に従うA値が770以上850以下、下記(2)式に従うB値が0.40以上であり、残部不可避的不純物およびFeの成分組成を有する鉄筋用鋼。
記
A=α+β+γ ・・・(1)
ここで、α=-334×[C]2+806×[C]+291
β=24×[Si]2+67×[Si]
γ=-4×[Cr]2+23×[Cr]-5
B=[Si]/[10×C] ・・・(2)
但し、上記の[ ]は、該括弧内成分の含有量(質量%) C: 0.37 mass% or more and 0.50 mass% or less,
Si: 1.75% by mass to 2.30% by mass,
Mn: 0.2% by mass or more and 1.0% by mass or less,
Cr: 0.01 mass% or more and 1.2 mass% or less,
Mo: 0.05 mass% or more and 1.0 mass% or less,
P: 0.025 mass% or less,
S: 0.025 mass% or less and O: 0.0015 mass% or less, A value according to the following (1) is 770 or more and 850 or less, B value according to the following formula (2) is 0.40 or more, and the balance of inevitable impurities and Fe Steel for reinforcing steel with component composition.
A = α + β + γ (1)
Here, α = −334 × [C] 2 + 806 × [C] +291
β = 24 × [Si] 2 + 67 × [Si]
γ = −4 × [Cr] 2 + 23 × [Cr] −5
B = [Si] / [10 × C] (2)
However, the above [] is the content (mass%) of the component in parentheses. - 前記成分組成が、さらに、
Al:0.50質量%以下、
Cu:1.0質量%以下および
Ni:2.0質量%以下
のうちから選ばれる1種または2種以上を含有する請求項1に記載の鉄筋用鋼。 The component composition further comprises:
Al: 0.50 mass% or less,
The steel for reinforcing bars according to claim 1, comprising one or more selected from Cu: 1.0 mass% or less and Ni: 2.0 mass% or less. - 前記成分組成は、さらに、
W:2.0質量%以下、
Nb:0.1質量%以下、
Ti:0.2質量%以下および
V:0.5質量%以下
のうちから選ばれる1種または2種以上を含有する請求項1または2に記載の鉄筋用鋼。 The component composition further includes:
W: 2.0 mass% or less,
Nb: 0.1% by mass or less,
The steel for reinforcing bars according to claim 1 or 2, comprising one or more selected from Ti: 0.2 mass% or less and V: 0.5 mass% or less. - 前記成分組成は、さらに、
B:0.005質量%以下
を含有することを特徴とする請求項1ないし3のいずれかに記載の鉄筋用鋼。 The component composition further includes:
B: Steel for reinforcing steel according to any one of claims 1 to 3, characterized by containing 0.005 mass% or less. - 表面から少なくとも20μmの厚み領域の硬さがHV250以下であり、表面から鋼材の径の1/4の深さ域の硬さがHRC40以下である請求項1ないし4のいずれかに記載の鉄筋用鋼。 The reinforcing steel for reinforcing bars according to any one of claims 1 to 4, wherein the hardness in the thickness region of at least 20 µm from the surface is HV250 or less, and the hardness in the depth region of 1/4 of the diameter of the steel material from the surface is HRC40 or less. steel.
- 請求項1ないし4のいずれかに記載の成分組成を有し、表面から少なくとも10μmの厚み領域の硬さがHV300以下である鉄筋。
A reinforcing bar having the component composition according to any one of claims 1 to 4 and having a hardness in a thickness region of at least 10 μm from the surface of HV300 or less.
Priority Applications (4)
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JP2014532775A JP5741773B2 (en) | 2012-08-31 | 2013-08-23 | Steel and rebar for rebar |
CN201380045017.2A CN104603310B (en) | 2012-08-31 | 2013-08-23 | Reinforcing bar steel and reinforcing bar |
IN727DEN2015 IN2015DN00727A (en) | 2012-08-31 | 2013-08-23 | |
KR1020157004634A KR101631522B1 (en) | 2012-08-31 | 2013-08-23 | Steel for reinforcing bars, and reinforcing bar |
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JP2012192529 | 2012-08-31 |
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JP (1) | JP5741773B2 (en) |
KR (1) | KR101631522B1 (en) |
CN (1) | CN104603310B (en) |
IN (1) | IN2015DN00727A (en) |
WO (1) | WO2014034070A1 (en) |
Cited By (1)
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WO2017222122A1 (en) * | 2016-06-21 | 2017-12-28 | 현대제철 주식회사 | Reinforcing bar and manufacturing method therefor |
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JP6135553B2 (en) * | 2014-02-28 | 2017-05-31 | Jfeスチール株式会社 | Reinforcing bar and method for manufacturing the same |
CN106521349B (en) * | 2016-11-10 | 2018-08-28 | 钢铁研究总院 | A kind of economical high-strength finish rolling deformed bar and production method |
CN111378902B (en) * | 2020-01-11 | 2021-05-14 | 武钢集团昆明钢铁股份有限公司 | Niobium-chromium microalloying produced 32-40mm HRB400E fine-grain high-toughness anti-seismic steel bar and preparation method thereof |
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-
2013
- 2013-08-23 IN IN727DEN2015 patent/IN2015DN00727A/en unknown
- 2013-08-23 KR KR1020157004634A patent/KR101631522B1/en active IP Right Grant
- 2013-08-23 JP JP2014532775A patent/JP5741773B2/en active Active
- 2013-08-23 WO PCT/JP2013/004997 patent/WO2014034070A1/en active Application Filing
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JPS59177317A (en) * | 1983-03-29 | 1984-10-08 | Daido Steel Co Ltd | Manufacture of supertough steel |
JPH0740331A (en) * | 1993-07-27 | 1995-02-10 | High Frequency Heattreat Co Ltd | Production of salt-resistant concrete columnar body |
JPH07173577A (en) * | 1993-11-04 | 1995-07-11 | Kobe Steel Ltd | High corrosion resistant steel for high strength spring |
JPH09324215A (en) * | 1996-06-07 | 1997-12-16 | Kobe Steel Ltd | Manufacture of high strength reinforcing bar excellent in yield elongation and bendability |
JP2002327243A (en) * | 2001-04-26 | 2002-11-15 | Kawatetsu Techno Wire Kk | Steel material for shear reinforcing bar with high strength, and weld-closed shear reinforcing bar with high strength |
JP2004076086A (en) * | 2002-08-15 | 2004-03-11 | Kobe Steel Ltd | High-strength steel component superior in delayed fracture resistance, and manufacturing method therefor |
JP2011246811A (en) * | 2010-03-29 | 2011-12-08 | Jfe Steel Corp | Spring steel and method of manufacturing the same |
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WO2017222122A1 (en) * | 2016-06-21 | 2017-12-28 | 현대제철 주식회사 | Reinforcing bar and manufacturing method therefor |
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IN2015DN00727A (en) | 2015-07-10 |
JPWO2014034070A1 (en) | 2016-08-08 |
KR20150034799A (en) | 2015-04-03 |
KR101631522B1 (en) | 2016-06-17 |
JP5741773B2 (en) | 2015-07-01 |
CN104603310A (en) | 2015-05-06 |
CN104603310B (en) | 2017-09-08 |
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