JP5802162B2 - Wire rod and steel wire using the same - Google Patents

Wire rod and steel wire using the same Download PDF

Info

Publication number
JP5802162B2
JP5802162B2 JP2012077003A JP2012077003A JP5802162B2 JP 5802162 B2 JP5802162 B2 JP 5802162B2 JP 2012077003 A JP2012077003 A JP 2012077003A JP 2012077003 A JP2012077003 A JP 2012077003A JP 5802162 B2 JP5802162 B2 JP 5802162B2
Authority
JP
Japan
Prior art keywords
less
amount
aln
wire
steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Fee Related
Application number
JP2012077003A
Other languages
Japanese (ja)
Other versions
JP2013204133A (en
Inventor
友信 石田
友信 石田
吉原　直
直 吉原
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to JP2012077003A priority Critical patent/JP5802162B2/en
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Priority to CN201380016256.5A priority patent/CN104204255B/en
Priority to PCT/JP2013/058566 priority patent/WO2013146676A1/en
Priority to EP13767810.8A priority patent/EP2832878B1/en
Priority to KR1020147026390A priority patent/KR101624447B1/en
Priority to ES13767810T priority patent/ES2743735T3/en
Priority to MX2014011471A priority patent/MX2014011471A/en
Publication of JP2013204133A publication Critical patent/JP2013204133A/en
Priority to ZA2014/06891A priority patent/ZA201406891B/en
Application granted granted Critical
Publication of JP5802162B2 publication Critical patent/JP5802162B2/en
Expired - Fee Related legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • 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
    • 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
    • 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
    • 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
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • 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
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length

Description

本発明は、ＰＣ鋼線やワイヤーロープ等に用いられる線材及びこれを用いた鋼線に関する。   The present invention relates to a wire used for a PC steel wire, a wire rope, and the like and a steel wire using the same.

土木・建築分野では、コンクリート部材の高強度化及び軽量化のニーズが強く、コンクリート部材の強化方法として、鋼線を用いてコンクリートに圧縮応力を与えるプレストレストコンクリート（以下、ＰＣと呼ぶ）が良く知られている。ＰＣに用いられる鋼線、すなわちＰＣ鋼線は、高強度であるほどＰＣの高強度化及び軽量化に寄与でき、現状ではＪＩＳ Ｇ３５３６で規定されるように、例えばφ１５．２ｍｍの７本より線で、最大試験力２６１ｋＮ程度のものが知られている。   In the field of civil engineering and construction, there is a strong need for high strength and light weight of concrete members, and as a method of strengthening concrete members, prestressed concrete (hereinafter referred to as PC) that applies compressive stress to concrete using steel wires is well known. It has been. The steel wire used for PC, that is, the PC steel wire, can contribute to higher strength and lighter weight of PC as the strength is higher. At present, as defined in JIS G3536, for example, seven strands of φ15.2 mm Thus, the one having a maximum test force of about 261 kN is known.

また、ＰＣ鋼線は、建築安全性等の観点からＪＩＳ規格以外にも種々の規格や推奨試験が定められている。特に、高強度ＰＣ鋼線を適用する上では、耐遅れ破壊特性を考慮することが重要である。遅れ破壊とは、応力が付加された状態で鋼材を長時間使用した場合に、鋼中に侵入した水素が鋼材表面の微細なキズ等に集中し、キズ周辺の組織を脆化させ、脆性破壊を引き起こす現象である。ＰＣ鋼線は、常に緊張された状態で使用されるため、遅れ破壊を起こす可能性があり、厳しい規格が設けられている。特に、強度の上昇に伴って遅れ破壊しやすくなることが良く知られており、高強度化しても遅れ破壊を抑制できる鋼材の開発が求められている。   In addition, various standards and recommended tests are defined for PC steel wires in addition to the JIS standard from the viewpoint of building safety and the like. In particular, when applying high strength PC steel wire, it is important to consider delayed fracture resistance. Delayed fracture means that when steel is used for a long time with stress applied, hydrogen that has penetrated into the steel concentrates on fine scratches on the surface of the steel, embrittles the structure around the scratch, and causes brittle fracture. It is a phenomenon that causes Since the PC steel wire is always used in a tensioned state, there is a possibility of causing delayed fracture, and strict standards are provided. In particular, it is well known that delayed fracture is likely to occur as the strength increases, and there is a demand for the development of a steel material that can suppress delayed fracture even when the strength is increased.

例えば、特許文献１では炭素量が０．６〜１．１％のＰＣ鋼線において、伸線加工後に４５０℃以上の温度でのブルーイングを行うことによって線材表層の板状セメンタイトを球状化し、耐遅れ破壊特性を向上させる技術が開示されている。しかし、特許文献１では、板状セメンタイトの球状化によって鋼線強度が低下し、強度の向上には限界があるため、２０００ＭＰａ以上の素線強度が得られないという問題があった。   For example, in Patent Document 1, in a PC steel wire having a carbon content of 0.6 to 1.1%, the plate-like cementite on the surface of the wire material is spheroidized by performing bluing at a temperature of 450 ° C. or higher after wire drawing, A technique for improving delayed fracture resistance is disclosed. However, Patent Document 1 has a problem that the strength of the steel wire decreases due to the spheroidization of the plate-like cementite, and there is a limit to the improvement of the strength.

特許文献２は、炭素量が０．６〜１．３％のＰＣ鋼線において、表層部に圧縮残留応力を付与した加工パーライト組織とすることによって、耐遅れ破壊特性を向上させる技術を開示している。しかし、特許文献２は、素線強度が１６００ＭＰａ程度までを対象とした技術であり、この技術によって、素線強度が例えば２０００ＭＰａ以上のより高い領域での水素拡散による耐遅れ破壊特性を十分に確保することは困難であると考えられる。   Patent Document 2 discloses a technique for improving delayed fracture resistance by forming a processed pearlite structure in which a compressive residual stress is applied to a surface layer portion in a PC steel wire having a carbon content of 0.6 to 1.3%. ing. However, Patent Document 2 is a technology for wire strength up to about 1600 MPa, and this technology sufficiently secures delayed fracture resistance due to hydrogen diffusion in a higher region where the wire strength is, for example, 2000 MPa or more. It seems difficult to do.

ＰＣ鋼線ではないが、特許文献３は、炭素量が０．６５〜１．２０％の軸受鋼において、５０〜３００ｎｍのＴｉ系又はＡｌ系の窒化物等を所定以上分散させて水素をトラップし、焼戻しマルテンサイト組織における耐遅れ破壊性を向上させる技術が開示されている。しかし、組織が異なれば水素の拡散挙動も異なり、トラップサイトとして適切な析出物の大きさ、量などが異なるため、この技術を主相がパーライト組織であるＰＣ鋼線などにそのまま適用することはできない。また、伸線加工後に焼入れ焼戻し処理を行う軸受鋼の製造工程と、パテンティング処理後に伸線加工を行うＰＣ鋼線の製造工程は大きく異なっており、製造工程における窒化物等の析出制御方法も異なる。   Although it is not a PC steel wire, Patent Document 3 traps hydrogen by dispersing a Ti-based or Al-based nitride of 50 to 300 nm or more in a bearing steel having a carbon content of 0.65 to 1.20%. In addition, a technique for improving delayed fracture resistance in a tempered martensite structure is disclosed. However, since the diffusion behavior of hydrogen is different for different structures and the size and amount of precipitates suitable as trap sites are different, it is not possible to apply this technology as it is to PC steel wires whose main phase is a pearlite structure. Can not. Also, the manufacturing process of bearing steel that performs quenching and tempering after the wire drawing process and the manufacturing process of PC steel wire that performs the wire drawing process after the patenting process are greatly different. Different.

特開２００４−３６０００５号公報JP 2004-360005 A 特開２００４−１３１７９７号公報JP 2004-131797 A 特許第３５９１２３６号公報Japanese Patent No. 3591236

本発明は、主相がパーライト組織である線材において、高強度化に伴う耐遅れ破壊特性の低下を抑制し、建築基準に適合する耐遅れ破壊特性を有する高強度ＰＣ鋼線、ワイヤーロープ等に用いることのできる線材を提供することを目的とする。   The present invention provides a high-strength PC steel wire, wire rope, etc. that has a delayed fracture resistance property that conforms to building standards, in a wire rod whose main phase is a pearlite structure, suppressing a decrease in the delayed fracture resistance property with increasing strength. It aims at providing the wire which can be used.

本発明者らは、主相がパーライト組織である線材において、水素トラップ効果を有する介在物について検討したところ、ＡｌＮ量を所定量以上確保するとともに、ＡｌＮの中でも１０〜２０μｍのサイズのＡｌＮを所定以上確保することが重要であることを見出した。すなわち、本発明の線材は、Ｃ：０．８〜１．２％（質量％の意味。以下、成分組成について同じ。）、Ｓｉ：０．１〜２．０％、Ｍｎ：０．１〜２．０％、Ｎ：０．００２〜０．０１０％、Ａｌ：０．０４〜０．１５％、Ｐ：０．０２％以下（０％を含む）、Ｓ：０．０２％以下（０％を含む）を含み、残部が鉄及び不可避不純物であり、Ａｌ量とＮ量が下記式（１）の関係を満足し、
［Ａｌ］≦−２．１×１０×［Ｎ］＋０．２５５ ・・・（１）
（但し、式（１）において［Ａｌ］、［Ｎ］は、それぞれＡｌ、Ｎの含有量（質量％）である。）
組織の主相がパーライトであるとともに、ＡｌＮ量が０．００５％以上であり、且つ、長さａと厚さｂの相乗平均（ａｂ）1/2で表されるＡｌＮの径ｄGMの最大値極値分布において、ｄGMが１０〜２０μｍであるＡｌＮの割合が、個数基準で５０％以上であることを特徴とする。上記線材は、固溶Ｎ量が０．００３％以下であることが好ましい。 The present inventors examined inclusions having a hydrogen trap effect in a wire having a pearlite structure as a main phase. As a result, the AlN content was ensured to be a predetermined amount or more, and AlN having a size of 10 to 20 μm was predetermined among AlN. We found that it is important to secure the above. That is, the wire rod of the present invention has C: 0.8 to 1.2% (meaning mass%, hereinafter the same for the component composition), Si: 0.1 to 2.0%, Mn: 0.1 to 0.1%. 2.0%, N: 0.002 to 0.010%, Al: 0.04 to 0.15%, P: 0.02% or less (including 0%), S: 0.02% or less (0 And the balance is iron and inevitable impurities, the amount of Al and the amount of N satisfy the relationship of the following formula (1),
[Al] ≦ −2.1 × 10 × [N] +0.255 (1)
(However, in the formula (1), [Al] and [N] are the contents (mass%) of Al and N, respectively.)
Maximum main phase of tissue with a pearlite, and the amount of AlN is 0.005% or more and the diameter d GM of AlN represented by geometric mean (ab) 1/2 of the length a and the thickness b in value extreme value distribution, the ratio of AlN d GM is 10~20μm, characterized in that a number basis of 50% or more. The wire rod preferably has a solid solution N content of 0.003% or less.

また、本発明は、更に（ａ）Ｃｒ：１．０％以下（０％を含まない）、Ｎｉ：１．０％以下（０％を含まない）、Ｃｏ：１．０％以下（０％を含まない）、Ｍｏ：１．０％以下（０％を含まない）、及びＣｕ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種、（ｂ）Ｂ：０．００５％以下（０％を含まない）、Ｎｂ：０．５％以下（０％を含まない）及びＶ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種を含有することも好ましい。   Further, the present invention further includes (a) Cr: 1.0% or less (excluding 0%), Ni: 1.0% or less (not including 0%), Co: 1.0% or less (0% At least one selected from the group consisting of Mo: 1.0% or less (not including 0%) and Cu: 0.5% or less (not including 0%), (b) B : Selected from the group consisting of 0.005% or less (not including 0%), Nb: 0.5% or less (not including 0%), and V: 0.5% or less (not including 0%) It is also preferable to contain at least one kind.

本発明は、上記線材から得られる鋼線も包含する。   The present invention also includes a steel wire obtained from the wire.

本発明によれば、Ａｌ量とＮ量を適切に調整し、さらにＡｌＮの総量と、所定サイズ（ｄGMが１０〜２０μｍ）のＡｌＮを適切に存在させているため、耐遅れ破壊特性に優れた線材を提供することができる。また、本発明の好ましい態様において、固溶Ｎ量を所定以下に調整することによって、鋼線の捻回特性を向上できる。 According to the present invention, the amount of Al and the amount of N are appropriately adjusted, and the total amount of AlN and AlN having a predetermined size (d GM is 10 to 20 μm) are appropriately present. Wire can be provided. Moreover, in the preferable aspect of this invention, the twist characteristic of a steel wire can be improved by adjusting the amount of solute N below predetermined.

本発明者らが検討したところ、主相がパーライト組織である線材においては、水素のトラップサイトとしてＡｌＮを所定量確保し、且つサイズが１０〜２０μｍであるＡｌＮを所定以上確保することが有効であることを見出した。   As a result of studies by the present inventors, it is effective to secure a predetermined amount of AlN as a hydrogen trap site and a predetermined amount or more of AlN having a size of 10 to 20 μm in a wire having a pearlite structure as a main phase. I found out.

ＡｌＮ量は、多いほど水素のトラップ効果が高まるため、０．００５％以上と定めた。ＡｌＮ量は、好ましくは０．００６％以上であり、より好ましくは０．００７％以上（特に０．０１％以上）である。ＡｌＮ量の上限は特に限定されないが、通常０．０４％程度である。   Since the amount of AlN increases as the hydrogen trapping effect increases, it is determined to be 0.005% or more. The amount of AlN is preferably 0.006% or more, more preferably 0.007% or more (particularly 0.01% or more). The upper limit of the amount of AlN is not particularly limited, but is usually about 0.04%.

また、サイズが１０〜２０μｍであるＡｌＮの個数を確保する指標として、本発明では最大値極値分布を用いる。まず、ＡｌＮのサイズとしては、ＡｌＮの長さａと厚さｂの相乗平均（ａｂ）1/2を用い、これをｄGM（μｍ）と表す。本発明において、ＡｌＮの長さａとは、線材長手方向のＡｌＮの長さを意味し、ＡｌＮの厚さｂとは、線材長手方向に垂直な方向のＡｌＮの長さを意味する。 In the present invention, the maximum value extreme value distribution is used as an index for securing the number of AlN having a size of 10 to 20 μm. First, as the size of AlN, the geometric mean (ab) 1/2 of the length a and the thickness b of AlN is used, and this is expressed as d GM (μm). In the present invention, the length “a” of AlN means the length of AlN in the longitudinal direction of the wire, and the thickness “b” of AlN means the length of AlN in the direction perpendicular to the longitudinal direction of the wire.

ｄGMの最大値極値分布とは、所定面積中に存在するＡｌＮのｄGMの最大値ｄGM（ｍａｘ）を測定し、これを複数視野について繰り返し、測定された複数のｄGM（ｍａｘ）について統計処理したものを意味する。本発明では、該極値分布において、ｄGM（ｍａｘ）が１０〜２０μｍであるＡｌＮの割合を、個数基準で５０％以上とする。ｄGMが２０μｍを超えるＡｌＮが多く存在すると、ＡｌＮの総個数が減少し、水素トラップ効果が十分に発揮できない。また、ｄGMが１０μｍ未満のＡｌＮは水素トラップ効果が少ない。従って、該極値分布において、ｄGM（ｍａｘ）が１０〜２０μｍであるＡｌＮの割合を、個数基準で５０％以上とすることによって、水素トラップに有効なＡｌＮを十分に確保できる。 d GM The maximum extreme value distribution, to measure the maximum value d GM (max) of d GM of AlN present in a given area, which is repeated for multiple viewing, measured more d GM (max) This means that statistical processing was performed on. In the present invention, in the extreme value distribution, the ratio of AlN having d GM (max) of 10 to 20 μm is set to 50% or more on the number basis. When the d GM is there are many AlN more than 20μm, the total number of AlN is reduced, the hydrogen trapping effect can not be sufficiently exhibited. Further, d GM is less than 10 [mu] m AlN is less hydrogen trapping effect. Therefore, in the extreme value distribution, by setting the ratio of AlN having d GM (max) of 10 to 20 μm to 50% or more based on the number, AlN effective for hydrogen trap can be sufficiently secured.

なお本発明において、主相がパーライトであるとは、組織の９５面積％以上がパーライト組織であることを意味する。パーライト組織の面積率は、好ましくは９７％以上であり、より好ましくは１００％である。   In the present invention, the main phase being pearlite means that 95% by area or more of the structure is a pearlite structure. The area ratio of the pearlite structure is preferably 97% or more, and more preferably 100%.

次に、本発明の線材の化学成分について説明する。   Next, the chemical components of the wire of the present invention will be described.

Ｃ：０．８〜１．２％
Ｃは、強度の上昇に有効な元素であり、Ｃ含有量の増加に伴って、線材及び冷間加工後の鋼線の強度が向上する。そこでＣ量は０．８％以上と定めた。Ｃ量は、好ましくは０．８５％以上であり、より好ましくは０．９０％以上である。しかし、Ｃ量が過剰になりすぎると、冷間伸線中に時効脆化を引き起こすため、鋼線の靭性が低下し、より線加工時に割れが発生するという問題がある。そこでＣ量は１．２％以下と定めた。Ｃ量は、好ましくは１．１％以下であり、より好ましくは１．０５％以下である。 C: 0.8 to 1.2%
C is an element effective for increasing the strength, and the strength of the wire rod and the steel wire after cold working is improved as the C content increases. Therefore, the C amount is set to 0.8% or more. The amount of C is preferably 0.85% or more, more preferably 0.90% or more. However, if the amount of C is excessive, aging embrittlement is caused during cold drawing, so that the toughness of the steel wire is lowered, and there is a problem that cracks occur during wire processing. Therefore, the C amount is set to 1.2% or less. The amount of C is preferably 1.1% or less, more preferably 1.05% or less.

Ｓｉ：０．１〜２．０％
Ｓｉは、脱酸剤の作用も有するが、特に線材の強度を向上させる作用及びリラクセーション特性を改善する作用を有するため有効な元素である。また、溶融亜鉛めっきを用いる場合には、Ｓｉはめっき時に生じる強度低下を抑える作用も有する。これら作用を有効に発揮させるため、Ｓｉ量を０．１％以上と定めた。Ｓｉ量は、好ましくは０．２％以上であり、より好ましくは０．４％以上である。一方、Ｓｉ量が過剰になりすぎると、冷間伸線性を悪化させ、断線率の増加を引き起こす。そこで、Ｓｉ量を２．０％以下と定めた。Ｓｉ量は好ましくは１．８％以下であり、より好ましくは１．５％以下である。 Si: 0.1 to 2.0%
Si has an action of a deoxidizer, but is an effective element because it has an action of improving the strength of the wire and an action of improving relaxation characteristics. In addition, when hot dip galvanization is used, Si also has an action of suppressing strength reduction that occurs during plating. In order to exhibit these effects effectively, the Si amount was determined to be 0.1% or more. The amount of Si is preferably 0.2% or more, and more preferably 0.4% or more. On the other hand, when the amount of Si becomes excessive, the cold drawing property is deteriorated and the disconnection rate is increased. Therefore, the Si amount is set to 2.0% or less. The amount of Si is preferably 1.8% or less, and more preferably 1.5% or less.

Ｍｎ：０．１〜２．０％
Ｍｎは、Ｓｉと同様に脱酸作用も有しているが、特に鋼中のＳをＭｎＳとして固定して、鋼の靭性及び延性を高める作用を有している。これらの作用を有効に発揮させるためにはＭｎ量は０．１％以上とする。Ｍｎ量は、好ましくは０．１５％以上であり、より好ましくは０．２％以上である。しかし、Ｍｎは偏析し易い元素であり、過剰に添加すると、Ｍｎ偏析部の焼入れ性が過剰に増大し、マルテンサイト等の過冷組織を生成させる恐れがある。そこで、Ｍｎ量は２．０％以下と定めた。Ｍｎ量は、好ましくは１．８％以下であり、より好ましくは１．５％以下である。 Mn: 0.1 to 2.0%
Mn has a deoxidizing action similar to Si, but has an effect of increasing the toughness and ductility of steel by fixing S in steel as MnS. In order to effectively exhibit these actions, the amount of Mn is set to 0.1% or more. The amount of Mn is preferably 0.15% or more, more preferably 0.2% or more. However, Mn is an element that easily segregates, and if added excessively, the hardenability of the Mn segregated part is excessively increased, and a supercooled structure such as martensite may be generated. Therefore, the amount of Mn is set to 2.0% or less. The amount of Mn is preferably 1.8% or less, more preferably 1.5% or less.

Ｎ：０．００２〜０．０１０％
Ｎは、本発明の特徴であるＡｌＮを形成するために重要な元素であり、０．００２％以上含有することが必要である。Ｎ量は、好ましくは０．００２５％以上であり、より好ましくは０．００３０％以上（特に０．００４０％以上）である。しかし、ＮはＣと同様に侵入型元素として鋼中に固溶し、歪み時効による脆化を引き起こすため、過剰に添加すると固溶Ｎ量が増大することによる捻回特性の低下を引き起こす。そこで、Ｎ量は０．０１０％以下と定めた。Ｎ量は、好ましくは０．００９０％以下であり、より好ましくは０．００８０％以下である。 N: 0.002 to 0.010%
N is an important element for forming AlN, which is a feature of the present invention, and must be contained in an amount of 0.002% or more. The amount of N is preferably 0.0025% or more, more preferably 0.0030% or more (particularly 0.0040% or more). However, N dissolves in steel as an interstitial element in the same manner as C and causes embrittlement due to strain aging. Therefore, when added excessively, the twisting characteristic is reduced due to an increase in the amount of dissolved N. Therefore, the N amount is determined to be 0.010% or less. The amount of N is preferably 0.0090% or less, and more preferably 0.0080% or less.

固溶Ｎ量：０．００３％以下
上述した通り、固溶Ｎは捻回特性の低下を引き起こすため、少ないほど好ましい。従って、固溶Ｎ量は０．００３％以下が好ましい。固溶Ｎ量は、より好ましくは０．００２％以下であり、さらに好ましくは０．００１％以下である。固溶Ｎ量は、Ａｌ、Ｂ、Ｎｂなどの窒化物形成元素の量と、Ｎ量を調整することなどによって、制御できる。 Solid solution N amount: 0.003% or less As described above, since the solid solution N causes a decrease in twisting characteristics, the smaller the amount, the better. Therefore, the amount of solute N is preferably 0.003% or less. The amount of solute N is more preferably 0.002% or less, and further preferably 0.001% or less. The amount of solute N can be controlled by adjusting the amount of nitride-forming elements such as Al, B, and Nb and the amount of N.

Ａｌ：０．０４〜０．１５％、且つ［Ａｌ］≦−２．１×１０×［Ｎ］＋０．２５５
Ａｌは、脱酸作用に加えて、本発明においてはＮと結合してＡｌＮを形成し、水素をトラップして耐遅れ破壊特性を向上させるために重要な元素である。また、前記ＡｌＮはピンニング効果によって結晶粒を微細化する効果も有する。このような効果を有効に発揮するため、Ａｌ量は０．０４％以上とする。Ａｌ量は、好ましくは０．０５％以上であり、より好ましくは０．０５５％以上である。一方、Ａｌ量が過剰になり、特にＮ量が多い領域でＡｌ量が過剰になると粗大なＡｌＮが生成し、ＡｌＮによる水素トラップ効果が低減する。従って、Ａｌ量の上限は０．１５％に定めるとともに、かつ下記式（１）の関係を満たすようにする。
［Ａｌ］≦−２．１×１０×［Ｎ］＋０．２５５ ・・・（１）
上記式（１）中、［Ａｌ］、［Ｎ］は、それぞれＡｌ、Ｎの含有量（質量％）を表している。式（１）は、Ｎ量、Ａｌ量を様々に変化させた際の耐遅れ破壊特性を調べた数多くの実験例から導き出された式である。Ａｌ量が式（１）の関係を満たすことによって、Ｎ量の多い領域では、Ａｌ量の上限がより厳格に制御され、粗大なＡｌＮの形成を抑制できる。Ａｌ量の上限は、好ましくは０．１４％以下であり、より好ましくは０．１２％以下である。 Al: 0.04-0.15% and [Al] ≦ −2.1 × 10 × [N] +0.255
In addition to the deoxidizing action, Al is an important element for bonding with N to form AlN and trapping hydrogen to improve delayed fracture resistance in the present invention. The AlN also has an effect of refining crystal grains by a pinning effect. In order to exhibit such an effect effectively, the amount of Al is made 0.04% or more. The amount of Al is preferably 0.05% or more, more preferably 0.055% or more. On the other hand, when the amount of Al becomes excessive, particularly when the amount of Al is excessive in a region where the amount of N is large, coarse AlN is generated, and the hydrogen trap effect by AlN is reduced. Therefore, the upper limit of the Al amount is set to 0.15% and satisfies the relationship of the following formula (1).
[Al] ≦ −2.1 × 10 × [N] +0.255 (1)
In the above formula (1), [Al] and [N] represent the contents (mass%) of Al and N, respectively. Expression (1) is an expression derived from a number of experimental examples in which the delayed fracture resistance characteristics when the N content and the Al content are changed in various ways. When the Al amount satisfies the relationship of the formula (1), the upper limit of the Al amount is more strictly controlled in a region where the N amount is large, and formation of coarse AlN can be suppressed. The upper limit of the amount of Al is preferably 0.14% or less, and more preferably 0.12% or less.

Ｐ：０．０２％以下（０％を含む）
Ｐは、旧オーステナイト粒界に偏析して粒界を脆化させ、疲労特性を低下させるため、その含有量は少なければ少ないほど好ましい。従って、Ｐ量は０．０２％以下とする。Ｐ量は、好ましくは０．０１５％以下であり、より好ましくは０．０１０％以下である。 P: 0.02% or less (including 0%)
P segregates at the prior austenite grain boundaries, embrittles the grain boundaries, and lowers fatigue characteristics. Therefore, the smaller the content, the better. Therefore, the P content is 0.02% or less. The amount of P is preferably 0.015% or less, more preferably 0.010% or less.

Ｓ：０．０２％以下（０％を含む）
Ｓは、Ｐと同様に旧オーステナイト粒界に偏析して粒界を脆化させ、疲労特性を低下させるため、その含有量は少なければ少ないほど好ましい。従って、Ｓ量は０．０２％以下とする。Ｓ量は、好ましくは０．０１５％以下であり、より好ましくは０．０１０％以下である。 S: 0.02% or less (including 0%)
S, like P, segregates at the prior austenite grain boundaries, embrittles the grain boundaries, and lowers fatigue characteristics. Therefore, the smaller the content, the better. Therefore, the S amount is 0.02% or less. The amount of S is preferably 0.015% or less, more preferably 0.010% or less.

本発明の線材の基本成分は上記の通りであり、残部は実質的に鉄である。但し、原料、資材、製造設備等の状況によって持ち込まれる不可避不純物が鋼中に含まれることは当然に許容される。さらに本発明の線材は、強度、靭性、延性等の特性をさらに向上させるため、必要に応じて下記の元素を含有していても良い。   The basic components of the wire of the present invention are as described above, and the balance is substantially iron. However, it is naturally allowed that inevitable impurities brought into the steel depending on the situation of raw materials, materials, manufacturing equipment, etc. are contained in the steel. Furthermore, the wire rod of the present invention may further contain the following elements as necessary in order to further improve properties such as strength, toughness and ductility.

Ｃｒ：１．０％以下（０％を含まない）、Ｎｉ：１．０％以下（０％を含まない）、
Ｃｏ：１．０％以下（０％を含まない）、Ｍｏ：１．０％以下（０％を含まない）、及びＣｕ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種
Ｃｒは、パーライトのラメラ間隔を微細化し、線材の強度や靭性を高める作用を有する。このような作用を有効に発揮させるため、Ｃｒ量は０．０５％以上が好ましい。Ｃｒ量は、より好ましくは０．１％以上であり、さらに好ましくは０．２％以上である。一方、Ｃｒ量が過剰になりすぎると、焼入れ性が向上して熱間圧延中の過冷組織を発生させる危険性が高まるため、Ｃｒ量は１．０％以下とすることが好ましい。Ｃｒ量は、より好ましくは０．６％以下であり、さらに好ましくは０．５％以下である。 Cr: 1.0% or less (not including 0%), Ni: 1.0% or less (not including 0%),
Selected from the group consisting of Co: 1.0% or less (excluding 0%), Mo: 1.0% or less (not including 0%), and Cu: 0.5% or less (not including 0%) At least one kind of Cr that has a function of reducing the lamella spacing of pearlite and increasing the strength and toughness of the wire. In order to effectively exhibit such action, the Cr content is preferably 0.05% or more. The amount of Cr is more preferably 0.1% or more, and further preferably 0.2% or more. On the other hand, if the amount of Cr becomes excessive, the hardenability is improved and the risk of generating a supercooled structure during hot rolling increases, so the Cr amount is preferably 1.0% or less. The amount of Cr is more preferably 0.6% or less, and further preferably 0.5% or less.

Ｎｉは、伸線後の鋼線の靭性を高める元素である。このような作用を有効に発揮させるため、Ｎｉ量は０．０５％以上が好ましく、より好ましくは０．１％以上であり、さらに好ましくは０．２％以上である。しかし、Ｎｉは過剰に添加してもその効果が飽和し、経済的に無駄である。従って、Ｎｉ量は１．０％以下が好ましく、より好ましくは０．７％以下、さらに好ましくは０．６％以下である。   Ni is an element that increases the toughness of the steel wire after wire drawing. In order to effectively exhibit such an action, the Ni content is preferably 0.05% or more, more preferably 0.1% or more, and further preferably 0.2% or more. However, even if Ni is added excessively, the effect is saturated and it is economically wasteful. Therefore, the Ni content is preferably 1.0% or less, more preferably 0.7% or less, and still more preferably 0.6% or less.

Ｃｏは、初析セメンタイトを低減し（特にＣ量が高い場合）、組織を均一なパーライト組織に制御しやすくするという作用を有する。この作用を有効に発揮するため、Ｃｏ量は０．０５％以上が好ましく、より好ましくは０．１％以上、さらに好ましくは０．２％以上である。しかし、Ｃｏは過剰に添加してもその効果が飽和し、経済的に無駄である。従って、Ｃｏ量は１．０％以下が好ましく、より好ましくは０．８％以下であり、さらに好ましくは０．６％以下である。   Co has the effect of reducing pro-eutectoid cementite (especially when the amount of C is high) and making it easy to control the structure to a uniform pearlite structure. In order to effectively exhibit this action, the Co content is preferably 0.05% or more, more preferably 0.1% or more, and further preferably 0.2% or more. However, even if Co is added excessively, the effect is saturated and it is economically wasteful. Therefore, the Co content is preferably 1.0% or less, more preferably 0.8% or less, and still more preferably 0.6% or less.

Ｍｏは、鋼線の耐食性を向上させる元素である。このような作用を有効に発揮するため、Ｍｏ量は０．０５％以上が好ましく、より好ましくは０．１％以上である。しかし、Ｍｏ量が過剰になると、熱間圧延時に過冷組織が発生しやすくなり、また延性も劣化する。そこでＭｏ量は１．０％以下が好ましく、より好ましくは０．５％以下であり、さらに好ましくは０．３％以下である。   Mo is an element that improves the corrosion resistance of the steel wire. In order to effectively exhibit such an action, the Mo amount is preferably 0.05% or more, more preferably 0.1% or more. However, when the amount of Mo becomes excessive, a supercooled structure is likely to occur during hot rolling, and ductility also deteriorates. Therefore, the Mo amount is preferably 1.0% or less, more preferably 0.5% or less, and still more preferably 0.3% or less.

Ｃｕは、鋼線の耐食性を向上させる元素である。このような作用を有効に発揮するため、Ｃｕ量は０．０５％以上が好ましく、より好ましくは０．０８％以上である。一方、Ｃｕ量が過剰になると、Ｓと反応して粒界部にＣｕＳを偏析させ、線材製造過程で疵を発生させる。このような影響を避けるため、Ｃｕ量は０．５％以下が好ましく、より好ましくは０．２％以下であり、さらに好ましくは０．１８％以下である。   Cu is an element that improves the corrosion resistance of the steel wire. In order to effectively exhibit such action, the amount of Cu is preferably 0.05% or more, more preferably 0.08% or more. On the other hand, when the amount of Cu becomes excessive, it reacts with S to segregate CuS at the grain boundary part and generate soot in the wire manufacturing process. In order to avoid such influence, the amount of Cu is preferably 0.5% or less, more preferably 0.2% or less, and further preferably 0.18% or less.

Ｂ：０．００５％以下（０％を含まない）、Ｎｂ：０．５％以下（０％を含まない）及びＶ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種
Ｂは、初析フェライトや初析セメンタイトの生成を妨げ、組織を均一なパーライト組織に制御しやすくする作用を有する。また、ＡｌＮが析出した後の余剰の固溶ＮをＢＮで固定することにより、固溶Ｎによる歪み時効を抑制して靭性を向上できる他、固溶Ｂ自体も靭性を向上させる作用がある。このような作用を有効に発揮させるため、Ｂ量は０．０００３％以上が好ましく、より好ましくは０．０００５％以上、さらに好ましくは０．００１％以上である。一方、Ｂ量が過剰になると、Ｆｅとの化合物であるＦｅ−Ｂ系化合物（例えばＦｅＢ2）が析出し、熱間圧延時の割れを引き起こすため、Ｂ量は０．００５％以下が好ましい。Ｂ量は、より好ましくは０．００４％以下であり、さらに好ましくは０．００３％以下である。 B: selected from the group consisting of 0.005% or less (not including 0%), Nb: 0.5% or less (not including 0%), and V: 0.5% or less (not including 0%) At least one type B has an effect of preventing the formation of pro-eutectoid ferrite and pro-eutectoid cementite and making it easy to control the structure to a uniform pearlite structure. Moreover, by fixing the excess solid solution N after precipitation of AlN with BN, the strain aging due to the solid solution N can be suppressed and the toughness can be improved, and the solid solution B itself also has the effect of improving the toughness. In order to exhibit such an action effectively, the amount of B is preferably 0.0003% or more, more preferably 0.0005% or more, and further preferably 0.001% or more. On the other hand, when the amount of B becomes excessive, an Fe—B compound (for example, FeB 2 ) that is a compound with Fe precipitates and causes cracking during hot rolling, so the amount of B is preferably 0.005% or less. The amount of B is more preferably 0.004% or less, and still more preferably 0.003% or less.

Ｎｂは、ＡｌＮが析出した後の余剰の固溶Ｎと窒化物を形成し、結晶粒微細化に寄与する他、固溶Ｎを固定することによる時効脆化の抑制効果も有する。このような作用を有効に発揮するため、Ｎｂ量は０．０１％以上が好ましく、より好ましくは０．０３％以上、さらに好ましくは０．０５％以上である。しかし、Ｎｂ量が過剰になってもその効果は飽和し、経済的に無駄であるため、Ｎｂ量は０．５％以下が好ましく、より好ましくは０．４％以下、さらに好ましくは０．２％以下である。   Nb forms an excessive solid solution N and nitride after AlN is precipitated, contributes to refinement of crystal grains, and also has an effect of suppressing aging embrittlement by fixing the solid solution N. In order to effectively exhibit such an action, the Nb content is preferably 0.01% or more, more preferably 0.03% or more, and still more preferably 0.05% or more. However, even if the Nb amount is excessive, the effect is saturated and economically useless, so the Nb amount is preferably 0.5% or less, more preferably 0.4% or less, and still more preferably 0.2%. % Or less.

ＶはＮｂと同様にＡｌＮが析出した後の余剰の固溶Ｎと窒化物を形成し、結晶粒微細化に寄与する他、固溶Ｎを固定することによる時効脆化の抑制効果も有する。このような作用を有効に発揮するため、Ｖ量は０．０１％以上が好ましく、より好ましくは０．０２％以上、さらに好ましくは０．０３％以上である。しかし、Ｖ量が過剰になってもその効果は飽和し、経済的に無駄であるため、Ｖ量は０．５％以下が好ましく、より好ましくは０．４％以下、さらに好ましくは０．２％以下である。   V forms an excessive solid solution N and nitride after precipitation of AlN, like Nb, and contributes to refinement of crystal grains, and also has an effect of suppressing aging embrittlement by fixing the solid solution N. In order to effectively exhibit such an action, the V amount is preferably 0.01% or more, more preferably 0.02% or more, and further preferably 0.03% or more. However, even if the amount of V is excessive, the effect is saturated and economically useless, so the amount of V is preferably 0.5% or less, more preferably 0.4% or less, and still more preferably 0.2%. % Or less.

線材（冷間伸線前のものを意味する）は、通常、化学成分を適切に制御した鋼を溶製、分塊圧延、熱間圧延する（さらに必要に応じてパテンティング処理する）ことにより製造できるが、本発明の線材においてＡｌＮの量と粒度分布（ＡｌＮのｄGMの最大値極値分布において、ｄGMが１０〜２０μｍであるＡｌＮの割合が、個数基準で５０％以上）を適切に制御するためには、Ａｌ及びＮの含有量を上述した範囲に適切に制御した上で、ＡｌＮが析出する温度範囲での熱履歴を適切に制御することが重要である。 Wire rods (meaning those before cold drawing) are usually obtained by melting, split-rolling, and hot-rolling (and patenting as necessary) steel with appropriately controlled chemical components. can be produced, (in maximum extreme value distribution d GM of AlN, the ratio of AlN d GM is 10~20μm is, more than 50% on a particle number basis) the amount and particle size distribution of the AlN in the wire rod of the present invention the appropriate Therefore, it is important to appropriately control the heat history in the temperature range in which AlN precipitates, while appropriately controlling the contents of Al and N within the above-described range.

ＡｌＮは、鋼中では約１３００℃以下で析出を開始し、温度が低下するにつれて析出量が増大し、約９００℃で完全に析出する。したがって、製造工程において鋼がこれらの温度範囲に曝され、ＡｌＮの析出挙動に大きく影響する分塊圧延及び熱間圧延の条件を適切に制御する必要がある。通常、分塊圧延後の冷却速度は遅いため、析出したＡｌＮが粗大化しやすく、これに対して熱間圧延後の冷却速度は相対的に速いので、析出したＡｌＮを微細にできる。   AlN starts to precipitate at about 1300 ° C. or less in steel, and the precipitation amount increases as the temperature decreases, and it completely precipitates at about 900 ° C. Therefore, it is necessary to appropriately control the conditions of the block rolling and the hot rolling, in which the steel is exposed to these temperature ranges in the production process and greatly affects the precipitation behavior of AlN. Usually, since the cooling rate after the block rolling is slow, the precipitated AlN tends to be coarsened. On the other hand, the cooling rate after the hot rolling is relatively fast, so that the precipitated AlN can be made fine.

具体的には、分塊圧延での加熱温度を１２３０〜１２８０℃、冷却速度を０．２℃／秒以上とする。分塊圧延時に高温で加熱し、且つ冷却速度を速めることでＡｌＮの析出及び粗大化を防ぐことができる。そこで分塊圧延温度は１２３０℃以上が好ましく、より好ましくは１２４０℃以上である。一方、分塊圧延温度が高すぎると焼き割れが生じるため、上限は１２８０℃以下とすることが好ましく、より好ましくは１２７０℃以下である。また冷却速度は０．２℃／秒以上が好ましく、より好ましくは０．４℃／秒以上、さらに好ましくは０．５℃／秒以上である。冷却速度の上限は特に限定されないが、例えば１．５℃／秒以下（好ましくは１．２℃／秒以下）である。   Specifically, the heating temperature in the ingot rolling is set to 1230 to 1280 ° C, and the cooling rate is set to 0.2 ° C / second or more. Precipitation and coarsening of AlN can be prevented by heating at a high temperature during block rolling and increasing the cooling rate. Therefore, the batch rolling temperature is preferably 1230 ° C or higher, more preferably 1240 ° C or higher. On the other hand, if the partial rolling temperature is too high, firing cracks occur, so the upper limit is preferably 1280 ° C. or less, more preferably 1270 ° C. or less. The cooling rate is preferably 0.2 ° C./second or more, more preferably 0.4 ° C./second or more, and further preferably 0.5 ° C./second or more. Although the upper limit of a cooling rate is not specifically limited, For example, it is 1.5 degrees C / sec or less (preferably 1.2 degrees C / sec or less).

さらに、分塊圧延により得られたビレットを熱間圧延した後、水冷等によって８５０〜９５０℃に冷却し、コイル状に載置する。前記したコイル状の線材の載置温度を低めにすることによって、微細（ｄGMが１０〜２０μｍ）なＡｌＮを析出できる。そこで、載置温度は９５０℃以下が好ましく、より好ましくは９４０℃以下、さらに好ましくは９２０℃以下である。一方、載置温度が低すぎると、水素トラップに寄与しない非常に微細なＡｌＮが数多く析出する。そこで、載置温度は８５０℃以上が好ましく、より好ましくは８７０℃以上、さらに好ましくは８９０℃以上である。 Furthermore, the billet obtained by the partial rolling is hot-rolled, then cooled to 850 to 950 ° C. by water cooling or the like, and placed in a coil shape. By the lower the placing置温of the coiled wire described above, fine (d GM is 10 to 20 [mu] m) can deposit an AlN. Therefore, the mounting temperature is preferably 950 ° C. or lower, more preferably 940 ° C. or lower, and further preferably 920 ° C. or lower. On the other hand, if the mounting temperature is too low, many very fine AlNs that do not contribute to the hydrogen trap are deposited. Therefore, the mounting temperature is preferably 850 ° C. or higher, more preferably 870 ° C. or higher, and further preferably 890 ° C. or higher.

また、前記した分塊圧延や熱間圧延の条件の少なくとも一部が外れるなどして、ＡｌＮの量や分布状態が適切に制御できない場合には、熱間圧延後に、適切な温度範囲でのパテンティング処理を行うことも有効である。パテンティング処理時の再加熱温度は８８０〜１０００℃、パテンティング温度は５３０〜６２０℃が好ましい。熱間圧延後のＡｌＮ量が少ない場合は、上記した再加熱温度を低め（例えば８８０〜９４０℃程度）に設定すれば、析出量を増加できる。また、熱間圧延後のＡｌＮが粗大化している場合には、再加熱温度を高め（例えば９４０〜１０００℃）に設定し、粗大化したＡｌＮを鋼中に一旦固溶させてから再度析出させれば良い。   In addition, if the amount and distribution of AlN cannot be controlled properly because at least a part of the conditions of the above-described block rolling and hot rolling are removed, a patent in the appropriate temperature range is obtained after hot rolling. It is also effective to perform the processing. The reheating temperature during the patenting treatment is preferably 880 to 1000 ° C, and the patenting temperature is preferably 530 to 620 ° C. When the amount of AlN after hot rolling is small, the amount of precipitation can be increased by setting the reheating temperature lower (for example, about 880 to 940 ° C.). In addition, when AlN after hot rolling is coarsened, the reheating temperature is set high (for example, 940 to 1000 ° C.), and the coarsened AlN is once dissolved in steel and then precipitated again. Just do it.

本発明の線材は、水素トラップサイトとして有効に作用できるＡｌＮを十分に確保しているため、これを用いたワイヤロープやＰＣ鋼線などの鋼線は、耐遅れ破壊特性に優れており、有用である。また、本発明はこのような鋼線も包含する。   Since the wire rod of the present invention sufficiently secures AlN that can effectively act as a hydrogen trap site, a steel wire such as a wire rope or PC steel wire using this has excellent delayed fracture resistance and is useful. It is. The present invention also includes such a steel wire.

以下、実施例を挙げて本発明をより具体的に説明する。本発明は以下の実施例によって制限を受けるものではなく、前記、後記の趣旨に適合し得る範囲で適当に変更を加えて実施することも勿論可能であり、それらはいずれも本発明の技術的範囲に包含される。   Hereinafter, the present invention will be described more specifically with reference to examples. The present invention is not limited by the following examples, and can of course be implemented with appropriate modifications within a range that can be adapted to the above-described gist. Included in the range.

表１に示す成分の鋼塊を、表２に示した条件で分塊圧延、熱間圧延して線材コイルに加工し、場合によっては更にパテンティング処理を行った。採取したサンプルの抽出残渣測定からＡｌＮの総量を、そして断面積の観察からＡｌＮの分布状態を評価した。   Steel ingots having the components shown in Table 1 were subjected to split rolling and hot rolling under the conditions shown in Table 2 to process into wire coils, and in some cases, patenting was further performed. The total amount of AlN was evaluated from the extraction residue measurement of the collected samples, and the distribution state of AlN was evaluated from observation of the cross-sectional area.

１．ＡｌＮの総量、及び固溶Ｎ量の測定
抽出残渣測定では、１０％アセチルアセトン溶液を用いた電解抽出残渣測定を行い、メッシュは０．１μｍのものを用い、残渣中のＡｌＮ量をブロムエステル法で測定した。また、インドフェノール吸収分光光度法を用いて、ＡｌＮを含めた窒素化合物の量を測定し、鋼中の全Ｎ量から差し引くことによって固溶Ｎ量を求めた。ブロムエステル法に用いた試料重量は３g、吸収分光法に用いた試料重量は０．５gとした。 1. Measurement of the total amount of AlN and the amount of dissolved N In extraction residue measurement, electrolytic extraction residue measurement using a 10% acetylacetone solution is performed, a mesh of 0.1 μm is used, and the amount of AlN in the residue is determined by the bromester method. It was measured. Moreover, the amount of nitrogen compounds including AlN was measured using the indophenol absorption spectrophotometry method, and the amount of dissolved N was determined by subtracting from the total amount of N in the steel. The sample weight used for the bromoester method was 3 g, and the sample weight used for the absorption spectroscopy was 0.5 g.

２．ＡｌＮの分布状態の測定
本測定では、線材の軸線を含み、且つ長手方向に平行な断面において、表層からＤ／４（Ｄは線材の直径）までの領域（２箇所）の合計が１４０ｍｍ2となるようにサンプルを切り出し（すなわち、サンプルの長さＬはＬ×Ｄ／４＋Ｌ×Ｄ／４＝Ｌ×Ｄ／２が１４０ｍｍ2となるように定められる）、前記断面において、ＪＩＳ Ｇ０５５５に従って、観察視野内で最大のＡｌＮの大きさを測定し、これを任意の２０視野について行った。なお、測定に際しては、ＪＩＳ Ｇ０５５１に規定されるＤ系及びＤＳ系介在物をＡｌＮとみなし、ＡｌＮの大きさとしてはＡｌＮの長さ（ａ）と厚さ（ｂ）の相乗平均（ａｂ）1/2を採用した。 2. Measurement of AlN distribution state In this measurement, the total area (two locations) from the surface layer to D / 4 (D is the diameter of the wire) is 140 mm 2 in the cross section including the axis of the wire and parallel to the longitudinal direction. The sample is cut out so that the length L of the sample is determined so that L × D / 4 + L × D / 4 = L × D / 2 is 140 mm 2, and the cross section is observed according to JIS G0555 The maximum AlN size was measured in the field of view and this was done for any 20 fields of view. In the measurement, the D-based and DS-based inclusions defined in JIS G0551 are regarded as AlN, and the size of AlN is the geometric mean (ab) 1 of the length (a) and thickness (b) of AlN. / 2 was adopted.

次に、得られた線材コイルを伸線加工して鋼線を作製し、鋼線の引張強度（素線強度）を測定するとともに、より線加工及びホットストレッチ処理を行って、ロープ強度、耐遅れ破壊特性、及び捻回特性を測定した。   Next, the obtained wire coil is drawn to produce a steel wire, and the tensile strength (strand strength) of the steel wire is measured. Delayed fracture characteristics and twist characteristics were measured.

３．鋼線の引張強度（素線強度）の測定
鋼線の引張強度を、ＪＩＳ Ｚ２２４１に従って測定した。 3. Measurement of tensile strength (strand strength) of steel wire The tensile strength of the steel wire was measured according to JIS Z2241.

４．ロープ強度の測定
ロープ強度の測定は、ＪＩＳ Ｇ３５３６に従い、引張試験の最大試験力を測定した。 4). Measurement of Rope Strength Rope strength was measured according to JIS G3536 by measuring the maximum test force of a tensile test.

５．耐遅れ破壊特性の測定
遅れ破壊特性は、文献１（fib bullten 30: Acceptance of stay cable systems using prestressing steels, January.2005）の記載に基づき、０．８ｐ．ｕ（０．８ｐ．ｕとは破断荷重の８０％を意味する）の荷重下で、２０質量％、５０℃のチオシアン酸アンモニウム溶液に浸漬し、１２サンプルについて破断するまでの時間を測定した。最小破断時間が２時間以上であり、かつ中央値破断時間が５時間以上である場合を合格とした。 5. Measurement of delayed fracture resistance Delayed fracture characteristics are based on the description in Reference 1 (fib bullten 30: Acceptance of stay cable systems using prestressing steels, January.2005). Under a load of u (0.8 p.u means 80% of the breaking load), it was immersed in an ammonium thiocyanate solution at 20% by mass and 50 ° C., and the time until breaking of 12 samples was measured. A case where the minimum breaking time was 2 hours or more and the median breaking time was 5 hours or more was regarded as acceptable.

６．捻回特性の測定
捻回特性は、ＦＫＫフレネシー工法のＦＫＫ ＨＴＳ−２６規格に基づき、捻回値３回以上を達成している場合を合格とした。 6). Measurement of twisting characteristics The twisting characteristics were determined to be acceptable when the twisting value of 3 times or more was achieved based on the FKK HTS-26 standard of the FKK Frenessy method.

Figure 0005802162
Figure 0005802162

Figure 0005802162
Figure 0005802162

Figure 0005802162
Figure 0005802162

試験Ｎｏ．１〜３、５、９、１０、１３〜２０、２８は、成分、組織、ＡｌＮの量、及びＡｌＮの分布状態がいずれも本発明の要件を満たしていたため、素線強度で２０００ＭＰａ以上（好ましくは２１００ＭＰａ以上）を達成でき、ＪＩＳ Ｇ３５３６に規定の基準を満たす高いより線強度を満たしつつ、耐遅れ破壊特性も良好であり、実用に耐える高強度より線が得られた。さらに、これら試験例は、好ましい要件である固溶Ｎ量の要件も満たしているため、捻回特性にも優れている。なお、例えば試験Ｎｏ．１５〜１８は、発明例中でも特に固溶Ｎ量が低減された例であり、その結果、捻回特性も非常に優れており、一方、発明例中で最も固溶Ｎ量が多かった試験Ｎｏ．９は、発明例中で捻回値が最も小さかった。   Test No. 1-3, 5, 9, 10, 13-20, and 28, the component, the structure, the amount of AlN, and the distribution state of AlN all satisfied the requirements of the present invention. 2100 MPa or higher), and satisfying the high wire strength satisfying the standard specified in JIS G3536, the delayed fracture resistance was also good, and the wire was obtained with high strength that can withstand practical use. Furthermore, since these test examples also satisfy the requirements for the solid solution N amount, which is a preferable requirement, they are excellent in twisting characteristics. For example, test No. Nos. 15 to 18 are examples in which the amount of solid solution N was particularly reduced among the inventive examples, and as a result, the twisting characteristics were also very excellent, while the test number having the largest amount of solid solution N in the invention examples. . No. 9 had the smallest twist value in the invention examples.

また、試験Ｎｏ．１０、１５、１７については、熱間圧延の載置温度が好ましい要件を外れているが、その後に適切なパテンティング処理を行っているため、本発明の要件を満たす線材が得られている。   In addition, Test No. For 10, 15, and 17, the hot rolling placement temperature deviates from the preferable requirement, but since appropriate patenting treatment is performed thereafter, a wire rod satisfying the requirements of the present invention is obtained.

一方、試験Ｎｏ．４、６〜８、１１、１２、２１〜２７は、本発明の要件のいずれかが満たされていなかった例である。   On the other hand, test no. 4, 6-8, 11, 12, 21-27 are examples in which any of the requirements of the present invention was not satisfied.

Ｎｏ．４は、分塊圧延時の加熱温度が低かったため、またＮｏ．６は分塊圧延後の冷却速度が遅かったため、いずれも粗大なＡｌＮが析出し、ＡｌＮの粒度分布が本発明の要件を満足せず、耐遅れ破壊特性が劣化した。   No. No. 4 was the same because No. 4 was heated at the time of ingot rolling. No. 6 had a slow cooling rate after the partial rolling, so that coarse AlN precipitated in all cases, the AlN particle size distribution did not satisfy the requirements of the present invention, and the delayed fracture resistance deteriorated.

Ｎｏ．７は、熱間圧延後の載置温度が高く、載置中のＡｌＮの析出が不十分となり、ＡｌＮ量及びＡｌＮの粒度分布がいずれも本発明の要件を満足せず、耐遅れ破壊性が劣化した。Ｎｏ．８は、熱間圧延後の載置温度が低く、ＡｌＮが過度に微細化したため、ＡｌＮの粒度分布が本発明の要件を満足せず、耐遅れ破壊性が劣化した。   No. No. 7, the mounting temperature after hot rolling is high, precipitation of AlN during mounting becomes insufficient, the amount of AlN and the particle size distribution of AlN do not satisfy the requirements of the present invention, and delayed fracture resistance Deteriorated. No. In No. 8, since the mounting temperature after hot rolling was low and AlN was excessively refined, the particle size distribution of AlN did not satisfy the requirements of the present invention, and the delayed fracture resistance deteriorated.

Ｎｏ．１１は、分塊圧延時の加熱温度が高すぎたために焼き割れを起こした。   No. No. 11 caused a burning crack because the heating temperature at the time of the block rolling was too high.

Ｎｏ．１２は、パテンティング処理温度が低すぎたため、ベイナイトとパーライトの混合組織となり、伸線性が低下した。なお、ベイナイトの分率は、およそ２０面積％であった。   No. In No. 12, since the patenting treatment temperature was too low, a mixed structure of bainite and pearlite was formed, and the drawability was lowered. In addition, the fraction of bainite was about 20 area%.

Ｎｏ．２１は、Ｃ量が多かった例であり、伸線中の時効脆化が顕著で、断線が多発した。Ｎｏ．２２は、Ｃ量が少なかった例であり、ＪＩＳ Ｇ３５３６で規定のより線Ｂ種の強度を達成できなかった。   No. No. 21 is an example in which the amount of C was large, aging embrittlement during wire drawing was remarkable, and wire breakage occurred frequently. No. No. 22 is an example in which the amount of C was small, and the strength of the type B strand specified in JIS G3536 could not be achieved.

Ｎｏ．２３は、Ａｌ量が少なかった例であり、ＡｌＮ量が十分確保できなかったために、耐遅れ破壊特性が劣化した。Ｎｏ．２４は、Ｎ量が本発明の範囲内ではあるが少なめであり、且つＡｌ量が多かった例であり、多量のＡｌ系酸化物が生成して、伸線時の断線が多発した。   No. No. 23 is an example in which the amount of Al was small, and since the amount of AlN could not be secured sufficiently, the delayed fracture resistance was deteriorated. No. No. 24 is an example in which the N content is within the range of the present invention, but less, and the Al content is large. A large amount of Al-based oxide was generated, and breakage during wire drawing occurred frequently.

Ｎｏ．２５は、Ｎ量が少なかった例であり、十分な量のＡｌＮ量が確保できないとともに、ＡｌＮの粒度分布も本発明の要件を満足できず、耐遅れ破壊特性が劣化した。Ｎｏ．２６はＮ量が多かった例であり、粗大なＡｌＮが析出したために耐遅れ破壊特性が劣化した。またＮｏ．２６は、固溶Ｎ量が本発明の好ましい要件を満たしていないため、捻回値が他の試験例に比べて最も小さい。   No. No. 25 was an example in which the amount of N was small, and a sufficient amount of AlN could not be secured, and the particle size distribution of AlN could not satisfy the requirements of the present invention, and the delayed fracture resistance was deteriorated. No. No. 26 is an example in which the amount of N was large, and the delayed fracture resistance deteriorated because coarse AlN precipitated. No. In No. 26, since the amount of solute N does not satisfy the preferable requirements of the present invention, the twist value is the smallest compared to other test examples.

Ｎｏ．２７は、Ｎ量が本発明で規定する範囲ではあるが多めであり、かつＡｌ量が式（１）の要件を満たしておらず、多かった例であり、粗大なＡｌＮが析出して、耐遅れ破壊特性が劣化した。   No. No. 27 is an example in which the amount of N is larger than the range specified in the present invention, and the amount of Al does not satisfy the requirement of formula (1), and is large. Delayed fracture characteristics deteriorated.

Claims (5)

Ｃ ：０．８〜１．２％（質量％の意味。以下、成分組成について同じ。）、
Ｓｉ：０．１〜２．０％、
Ｍｎ：０．１〜２．０％、
Ｎ ：０．００２〜０．０１０％、
Ａｌ：０．０４〜０．１５％、
Ｐ ：０．０２％以下（０％を含む）、
Ｓ ：０．０２％以下（０％を含む）を含み、残部が鉄及び不可避不純物であり、
Ａｌ量とＮ量が下記式（１）の関係を満足し、
［Ａｌ］≦−２．１×１０×［Ｎ］＋０．２５５ ・・・（１）
（但し、式（１）において［Ａｌ］、［Ｎ］は、それぞれＡｌ、Ｎの含有量（質量％）である。）
組織の主相がパーライトであるとともに、
ＡｌＮ量が０．００５％以上であり、且つ、線材長手方向のＡｌＮの長さａと線材長手方向に垂直な方向のＡｌＮの長さである厚さｂの相乗平均（ａｂ）1/2で表されるＡｌＮの径ｄGMの最大値極値分布において、ｄGMが１０〜２０μｍであるＡｌＮの割合が、個数基準で５０％以上であることを特徴とする線材。 C: 0.8 to 1.2% (meaning mass%, hereinafter the same for the component composition),
Si: 0.1 to 2.0%,
Mn: 0.1 to 2.0%,
N: 0.002 to 0.010%,
Al: 0.04 to 0.15%,
P: 0.02% or less (including 0%),
S: 0.02% or less (including 0%), the balance being iron and inevitable impurities,
The amount of Al and the amount of N satisfy the relationship of the following formula (1),
[Al] ≦ −2.1 × 10 × [N] +0.255 (1)
(However, in the formula (1), [Al] and [N] are the contents (mass%) of Al and N, respectively.)
The main phase of the organization is perlite,
And the amount of AlN is 0.005% or more and, in the wire longitudinal geometric mean of the length length of a and the wire perpendicular to the longitudinal direction direction AlN is thickness b of AlN (ab) 1/2 In the maximum value extreme value distribution of the diameter d GM of AlN expressed, the ratio of AlN having a d GM of 10 to 20 μm is 50% or more on a number basis. 固溶Ｎ量が０．００３％以下である請求項１に記載の線材。   The wire according to claim 1, wherein the solid solution N amount is 0.003% or less. 更に、
Ｃｒ：１．０％以下（０％を含まない）、
Ｎｉ：１．０％以下（０％を含まない）、
Ｃｏ：１．０％以下（０％を含まない）、
Ｍｏ：１．０％以下（０％を含まない）、及び
Ｃｕ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種を含有する請求項１又は２に記載の線材。 Furthermore,
Cr: 1.0% or less (excluding 0%),
Ni: 1.0% or less (excluding 0%),
Co: 1.0% or less (excluding 0%),
3. The composition according to claim 1, comprising at least one selected from the group consisting of Mo: 1.0% or less (not including 0%) and Cu: 0.5% or less (not including 0%). Wire rod. 更に、
Ｂ ：０．００５％以下（０％を含まない）、
Ｎｂ：０．５％以下（０％を含まない）、及び
Ｖ：０．５％以下（０％を含まない）よりなる群から選択される少なくとも１種を含有する請求項１〜３のいずれかに記載の線材。 Furthermore,
B: 0.005% or less (excluding 0%),
Nb: 0.5% or less (not including 0%), and V: 0.5% or less (not including 0%), at least one selected from the group consisting of any one of claims 1 to 3 Crab wire. 請求項１〜４のいずれかに記載の線材から得られる鋼線。   The steel wire obtained from the wire in any one of Claims 1-4.
JP2012077003A 2012-03-29 2012-03-29 Wire rod and steel wire using the same Expired - Fee Related JP5802162B2 (en)

Priority Applications (8)

Application Number Priority Date Filing Date Title
JP2012077003A JP5802162B2 (en) 2012-03-29 2012-03-29 Wire rod and steel wire using the same
PCT/JP2013/058566 WO2013146676A1 (en) 2012-03-29 2013-03-25 Wire rod and steel wire using same
EP13767810.8A EP2832878B1 (en) 2012-03-29 2013-03-25 Wire rod and steel wire using same
KR1020147026390A KR101624447B1 (en) 2012-03-29 2013-03-25 Wire rod and steel wire using same
CN201380016256.5A CN104204255B (en) 2012-03-29 2013-03-25 Wire rod and use its steel wire
ES13767810T ES2743735T3 (en) 2012-03-29 2013-03-25 Wire rod and steel cable using the same
MX2014011471A MX2014011471A (en) 2012-03-29 2013-03-25 Wire rod and steel wire using same.
ZA2014/06891A ZA201406891B (en) 2012-03-29 2014-09-19 Wire rod and steel wire using same

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2012077003A JP5802162B2 (en) 2012-03-29 2012-03-29 Wire rod and steel wire using the same

Publications (2)

Publication Number Publication Date
JP2013204133A JP2013204133A (en) 2013-10-07
JP5802162B2 true JP5802162B2 (en) 2015-10-28

Family

ID=49259927

Family Applications (1)

Application Number Title Priority Date Filing Date
JP2012077003A Expired - Fee Related JP5802162B2 (en) 2012-03-29 2012-03-29 Wire rod and steel wire using the same

Country Status (8)

Country Link
EP (1) EP2832878B1 (en)
JP (1) JP5802162B2 (en)
KR (1) KR101624447B1 (en)
CN (1) CN104204255B (en)
ES (1) ES2743735T3 (en)
MX (1) MX2014011471A (en)
WO (1) WO2013146676A1 (en)
ZA (1) ZA201406891B (en)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103710640B (en) * 2013-12-30 2016-05-25 钢铁研究总院 A kind of economy type modifier treatment 690MPa grade high strength and high toughness steel plate
KR101882123B1 (en) * 2014-06-04 2018-07-25 신닛테츠스미킨 카부시키카이샤 Steel wire
CN105886948A (en) * 2015-01-26 2016-08-24 鞍钢股份有限公司 Production method for 35Si2Cr steel bar for high-speed railway ballastless track
CN107406950B (en) * 2015-03-30 2020-04-14 株式会社神户制钢所 High-carbon steel wire rod and steel wire having excellent drawability
JP6416709B2 (en) * 2015-07-21 2018-10-31 新日鐵住金株式会社 High strength PC steel wire
JP6416708B2 (en) * 2015-07-21 2018-10-31 新日鐵住金株式会社 High strength PC steel wire
KR101867677B1 (en) * 2016-07-22 2018-06-15 주식회사 포스코 Steel wire rod having enhanced delayed fracture resistance and method for manufacturing the same
CN110462090A (en) * 2017-03-31 2019-11-15 日本制铁株式会社 Railway wheel
KR102117400B1 (en) * 2018-08-31 2020-06-01 주식회사 포스코 Steel wire rod for cold forging, processed good using the same, and methods for manufacturing thereof
JP7469642B2 (en) 2020-05-21 2024-04-17 日本製鉄株式会社 High-strength steel wire

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS60149732A (en) * 1984-01-13 1985-08-07 Sumitomo Electric Ind Ltd Heat treatment of steel wire rod
JPS61261430A (en) * 1985-05-14 1986-11-19 Shinko Kosen Kogyo Kk Manufacture of high strength and toughness steel wire
JPH05171267A (en) * 1991-09-27 1993-07-09 Nippon Steel Corp Production of high toughness pearlite steel
JP3591236B2 (en) 1997-09-04 2004-11-17 日本精工株式会社 Rolling bearing
JP4146205B2 (en) 2002-10-10 2008-09-10 新日本製鐵株式会社 PC steel wire having good delayed fracture resistance, its manufacturing method, and PC stranded wire
JP4267376B2 (en) 2003-06-04 2009-05-27 新日本製鐵株式会社 High strength PC steel wire with excellent delayed fracture characteristics and method for producing the same
EP1728883A4 (en) * 2004-03-02 2009-12-16 Honda Motor Co Ltd High strength bolt excellent in characteristics of resistance to delayed fracture and resistance to relaxation
US8864920B2 (en) * 2005-06-29 2014-10-21 Nippon Steel & Sumitomo Metal Corporation High strength wire rod excellent in drawability and method of producing same
KR101011565B1 (en) * 2005-06-29 2011-01-27 신닛뽄세이테쯔 카부시키카이샤 High-strength wire rod excelling in wire drawing performance and process for producing the same
EP2062991A4 (en) * 2007-01-31 2013-01-16 Nippon Steel Corp Plated steel wire for pws excelling in torsion property and process for producing the same
JP5000367B2 (en) * 2007-04-13 2012-08-15 新日本製鐵株式会社 High strength galvanized bolt with excellent hydrogen embrittlement resistance
JP5315790B2 (en) * 2008-05-19 2013-10-16 新日鐵住金株式会社 High strength PC steel wire with excellent delayed fracture resistance
KR101302291B1 (en) * 2009-06-25 2013-09-03 신닛테츠스미킨 카부시키카이샤 HIGH-STRENGTH Zn-Al-PLATED STEEL WIRE FOR BRIDGES WHICH HAS EXCELLENT CORROSION RESISTANCE AND FATIGUE PROPERTIES, AND PROCESS FOR PRODUCTION THEREOF
WO2011089782A1 (en) * 2010-01-25 2011-07-28 新日本製鐵株式会社 Wire material, steel wire, and process for production of wire material
WO2011125447A1 (en) * 2010-04-01 2011-10-13 株式会社神戸製鋼所 High-carbon steel wire with excellent suitability for wiredrawing and fatigue property after wiredrawing
JP5521885B2 (en) * 2010-08-17 2014-06-18 新日鐵住金株式会社 Steel wire for machine parts with high strength and excellent hydrogen embrittlement resistance, machine parts and method for producing the same

Also Published As

Publication number Publication date
EP2832878A4 (en) 2016-04-27
KR101624447B1 (en) 2016-05-25
ZA201406891B (en) 2016-01-27
EP2832878A1 (en) 2015-02-04
EP2832878B1 (en) 2019-08-14
ES2743735T3 (en) 2020-02-20
CN104204255A (en) 2014-12-10
WO2013146676A1 (en) 2013-10-03
KR20140129239A (en) 2014-11-06
JP2013204133A (en) 2013-10-07
CN104204255B (en) 2016-08-24
MX2014011471A (en) 2014-12-08

Similar Documents

Publication Publication Date Title
JP5802162B2 (en) Wire rod and steel wire using the same
JP5833485B2 (en) Wire rod and steel wire using the same
JP5135557B2 (en) High-strength steel material and high-strength bolt excellent in delayed fracture resistance
JP5177323B2 (en) High-strength steel material and high-strength bolt excellent in delayed fracture resistance
JP6180351B2 (en) High strength steel wire and high strength steel wire with excellent stretchability
JP5846080B2 (en) High-strength steel with excellent delayed fracture resistance
WO2016002413A1 (en) Wire material for steel wire, and steel wire
CA2812469A1 (en) High carbon steel wire rod having excellent drawability
JP5251632B2 (en) High strength steel material with excellent delayed fracture resistance, high strength bolt and manufacturing method thereof
WO2016158901A1 (en) High-carbon steel wire material with excellent wire drawability, and steel wire
JP5977699B2 (en) High-strength wire for high-strength steel wire, high-strength steel wire, high-strength galvanized steel wire, and manufacturing method thereof
JP6288265B2 (en) Steel wire
JP5741773B2 (en) Steel and rebar for rebar
JP2019123905A (en) Two-phase stainless steel wire for prestressed concrete tendon, two-phase stainless steel wire, and prestressed concrete tendon
WO2016002414A1 (en) Wire material for steel wire, and steel wire
CN108350544B (en) Steel wire
JP6135553B2 (en) Reinforcing bar and method for manufacturing the same
JP6682863B2 (en) High carbon steel wire rod and high carbon steel wire
JPH06336648A (en) High strength pc bar wire excellent in delayed fracture resistance and its production
JP2018162523A (en) Wire material for steel wire, and steel wire
JP2018162524A (en) Wire material for steel wire, and steel wire

Legal Events

Date Code Title Description
A621 Written request for application examination

Free format text: JAPANESE INTERMEDIATE CODE: A621

Effective date: 20140901

A131 Notification of reasons for refusal

Free format text: JAPANESE INTERMEDIATE CODE: A131

Effective date: 20150623

A521 Request for written amendment filed

Free format text: JAPANESE INTERMEDIATE CODE: A523

Effective date: 20150805

TRDD Decision of grant or rejection written
A01 Written decision to grant a patent or to grant a registration (utility model)

Free format text: JAPANESE INTERMEDIATE CODE: A01

Effective date: 20150825

A61 First payment of annual fees (during grant procedure)

Free format text: JAPANESE INTERMEDIATE CODE: A61

Effective date: 20150828

R150 Certificate of patent or registration of utility model

Ref document number: 5802162

Country of ref document: JP

Free format text: JAPANESE INTERMEDIATE CODE: R150

LAPS Cancellation because of no payment of annual fees