WO2012093715A1 - Steel wire material and method for producing same - Google Patents
Steel wire material and method for producing same Download PDFInfo
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- WO2012093715A1 WO2012093715A1 PCT/JP2012/050155 JP2012050155W WO2012093715A1 WO 2012093715 A1 WO2012093715 A1 WO 2012093715A1 JP 2012050155 W JP2012050155 W JP 2012050155W WO 2012093715 A1 WO2012093715 A1 WO 2012093715A1
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- 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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
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- 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
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- 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
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- 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
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- 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
- C21D9/54—Furnaces for treating strips or wire
- C21D9/56—Continuous furnaces for strip or wire
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- 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
- C21D9/54—Furnaces for treating strips or wire
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- C21D9/562—Details
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Definitions
- the present invention relates to a steel wire and a method for producing the same, and in particular, a hot-rolled steel wire formed with a thin scale that can be easily removed by mechanical descaling without being peeled off during cooling after hot rolling or during storage and transportation. (Hereinafter simply referred to as “wire”) and its manufacturing method.
- a scale is usually formed on the surface of the wire manufactured by hot rolling, and it is necessary to remove this scale before subjecting the wire to secondary processing such as wire drawing.
- a method for removing scale before such secondary processing a batch-type pickling method has been used in the past, but in recent years, from the viewpoint of pollution problems and cost reduction, a mechanical descaling (hereinafter referred to as MD) method is used. Is being used. Therefore, it is requested
- Patent Documents 1 to 5 can be cited as methods for producing a wire having a scale with good MD properties.
- the scale amount remaining in the wire after MD is reduced by forming a thick scale with a high FeO ratio.
- Patent Literature 3 by reducing the interface roughness, the propagation of cracks generated at the scale interface is promoted, and the residual scale amount is reduced.
- Patent Documents 4 and 5 the peelability of the scale is improved by controlling the area ratio of the pores in the scale.
- Patent Documents 1 to 5 described above have the following problems.
- the yield is lowered, and the scale is peeled off during the cooling process, storage and transportation, and rust is generated.
- the scale is thick, it is difficult to completely remove the scale even if bending strain is applied to the wire by the MD method and further the surface of the wire is brushed. That is, unlike the batch type pickling method, the MD method is difficult to remove the entire scale uniformly and stably, and even if MD is applied to a wire having a thick scale, the surface of the wire In some cases, finely crushed scale powder is scattered. In this way, when the residual scale remaining locally increases, problems such as wrinkles due to poor lubrication and a decrease in the die life may occur in secondary processing such as wire drawing.
- Patent Documents 1 to 5 do not consider any scale peeling due to the compressive stress generated during cooling, and the scale peels during cooling, storage, or transportation, and rust is generated on the wire before MD. There was a problem to do.
- the present invention has been made in view of the above circumstances, and the purpose thereof is a wire rod formed with a scale that does not peel off during cooling after hot rolling or during storage / transport, but easily peels off during MD, And a manufacturing method thereof.
- the steel wire rod according to the present invention that has achieved the above-mentioned problems is: C: 0.05 to 1.2% (meaning mass%, hereinafter the same for chemical components), Si: 0.01 to 0.5%, Mn: 0.1 to 1.5%, P: 0.02% or less (not including 0%), S: 0.02% or less (not including 0%), N: 0.005% or less (0% Steel wire with the balance being iron and inevitable impurities, the scale having a thickness of 7.0 ⁇ m or less, and the FeO ratio in the scale being 30 to 80% by volume, Fe 2 SiO 4 ratio is less than 0.1% by volume.
- the steel wire rod according to the present invention includes (a) Cr: 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%), (b) Cu as required. : 0.2% or less (excluding 0%), (c) at least one element selected from the group consisting of Nb, V, Ti, Hf, and Zr is 0.1% or less in total (0 %), (D) Al: 0.1% or less (not including 0%), (e) B: 0.005% or less (not including 0%), (f) Ca: 0.01 % Or less (not including 0%) and / or Mg: 0.01% or less (not including 0%) may be contained.
- the present invention provides a mixed gas of oxygen and an inert gas in which the steel having any one of the chemical components described above is rolled up at 750 to 880 ° C. after hot rolling and the oxygen fraction is less than 20% by volume, Or the manufacturing method of the steel wire which cools, spraying an inert gas is also included.
- the inert gas is preferably nitrogen.
- the wire rod of the present invention has a thin (7.0 ⁇ m or less) scale in which the FeO ratio is appropriately controlled (30 to 80% by volume) within a predetermined range. Therefore, the scale does not peel off during cooling after hot rolling or during storage / transport, and rusting can be prevented. Furthermore, according to the present invention, since the scale is easily peeled off at the time of MD, sufficient peelability can be ensured with a simple descaling device, and adverse effects during secondary processing such as wire drawing (the surface of the wire surface due to leftover of the scale, It is possible to provide a high quality steel wire rod without causing poor lubrication. Further, since the scale loss is small, the yield can be maintained high.
- FIG. 1 is a graph showing the relationship between the FeO ratio in the scale and the residual scale area ratio after MD.
- FIG. 2 is a graph showing the relationship between the scale thickness and the scale peeling rate of the rolled material.
- the MD method is a method in which a wire is distorted to cause cracks in the scale or at the interface between the ground iron and the scale, and the scale is peeled off.
- the ratio of FeO in the scale has been improved. This is because the adhesion strength of FeO to the ground iron is smaller than that of Fe 2 O 3 or Fe 3 O 4 , so increasing the FeO ratio in the scale is effective in improving the scale peelability during MD. Because it is considered.
- a thick scale peels off during the cooling process, storage and transportation. That is, it was extremely difficult to reduce the thickness of the scale and to secure the FeO ratio in the scale.
- the coiling temperature after hot rolling is set to a relatively low temperature, and then cooling while injecting a mixed gas or inert gas of oxygen and inert gas having a low oxygen fraction.
- the scale can be thinned and the FeO ratio in the scale can be secured at a predetermined level or more.
- the scale thickness is preferably 6.5 ⁇ m or less, more preferably 6.0 ⁇ m or less (particularly 5.5 ⁇ m or less).
- the lower limit of the scale thickness is not particularly limited, but is usually about 0.9 ⁇ m.
- FIG. 1 is a graph showing the relationship between the FeO ratio in the scale and the area ratio of the scale remaining after MD.
- FIG. 1 shows that if the FeO ratio in the scale is 30 to 80% by volume, the amount of residual scale after MD can be sufficiently reduced.
- the FeO ratio is preferably 35% by volume or more and 75% by volume or less, more preferably 40% by volume or more and 70% by volume or less, and further preferably 45% by volume or more and 65% by volume or less.
- the proportion of Fe 2 SiO 4 (firelite) in the scale is less than 0.1% by volume.
- Fe 2 SiO 4 is generated excessively, it is generated non-uniformly at the interface between the scale and the ground iron, and the scale is exfoliated unevenly during MD, so that the MD property deteriorates.
- the Fe 2 SiO 4 ratio is preferably 0.09% by volume or less, more preferably 0.08% by volume or less, and still more preferably 0.07% by volume or less.
- Fe 2 SiO 4 in the scale is an oxide that is brittle and easily peeled off, and if it is a trace amount, it is uniformly thinly formed, so that it has an effect of improving MD properties. In order to effectively exhibit such an action, it is preferable to ensure 0.01% by volume or more, more preferably 0.02% by volume or more, and further preferably 0.03% by volume or more.
- the scale in the present invention includes Fe 2 O 3 , Fe 3 O 4 and the like in addition to FeO and Fe 2 SiO 4 .
- the amount of residual scale after MD can be reduced to 30% or less in terms of the area ratio with respect to the amount of scale before MD. This corresponds to approximately 0.05% by mass or less in the remaining scale amount with respect to the mass of the steel wire.
- the residual scale amount is preferably 25 area% or less, more preferably 20 area% or less.
- a steel having the chemical composition described later is hot-rolled, wound at a relatively low temperature (750 to 880 ° C.), and then mixed with oxygen and an inert gas having a low oxygen fraction. It is important to cool while spraying gas or inert gas.
- the scale can be thinned by winding at a low temperature. Further, by blowing and cooling a gas having a low oxygen fraction or containing no oxygen as described above, the generated FeO can be secured at a predetermined level or more without changing to Fe 3 O 4 .
- the coiling temperature after hot rolling exceeds 880 ° C.
- the scale thickness exceeds 7.0 ⁇ m
- the FeO ratio in the scale exceeds 80% by volume
- the MD property deteriorates.
- the coiling temperature exceeds 880 ° C., it may exceed 0.1% by volume, and Fe 2 SiO 4 (firelight) is generated unevenly at the interface between the scale and the ground iron. Unevenly peels off and MD properties deteriorate.
- the coiling temperature is lower than 750 ° C., the FeO ratio cannot be ensured by 30% by volume or more, and the MD property deteriorates.
- the winding temperature is preferably 770 ° C. or higher and 875 ° C. or lower, more preferably 790 ° C. or higher and 860 ° C. or lower.
- Cooling after hot rolling is performed while spraying a mixed gas of oxygen and an inert gas having an oxygen fraction of less than 20% by volume, or an inert gas.
- the oxygen fraction is preferably 10% by volume or less, more preferably 5% by volume or less, and still more preferably 0% by volume (that is, only inert gas).
- the inert gas include argon, nitrogen and the like, preferably nitrogen.
- the cooling stop temperature of the cooling performed by spraying the gas is not particularly limited. For example, the cooling may be performed while spraying the gas up to about 550 to 650 ° C., and then cooling to room temperature in the atmosphere.
- C 0.05 to 1.2% C is an element that greatly affects the mechanical properties of steel.
- the C content was set to 0.05% or more.
- the amount of C is preferably 0.15% or more, and more preferably 0.3% or more.
- the C amount is set to 1.2% or less.
- the amount of C is preferably 1.1% or less, and more preferably 1.0% or less.
- Si 0.01 to 0.5% Si is an element necessary for deoxidation of steel, and if its content is too small, the production of Fe 2 SiO 4 (firelight) becomes insufficient and the MD property deteriorates. Therefore, the Si amount is determined to be 0.01% or more.
- the amount of Si is preferably 0.1% or more, and more preferably 0.2% or more.
- the Si amount is set to 0.5% or less.
- the amount of Si is preferably 0.45% or less, and more preferably 0.4% or less.
- Mn 0.1 to 1.5% Mn is an element useful for securing the hardenability of steel and increasing the strength. In order to effectively exhibit such an action, the amount of Mn was determined to be 0.1% or more. The amount of Mn is preferably 0.2% or more, and more preferably 0.4% or more. On the other hand, when the amount of Mn is excessive, segregation occurs in the cooling process after hot rolling, and a supercooled structure (such as martensite) that is harmful to wire drawing workability is likely to occur. Therefore, the amount of Mn is set to 1.5% or less. The amount of Mn is preferably 1.4% or less, more preferably 1.2% or less.
- P 0.02% or less (excluding 0%)
- P is an element that deteriorates the toughness and ductility of steel.
- the P content is set to 0.02% or less.
- the amount of P is preferably 0.01% or less, and more preferably 0.005% or less.
- the lower limit of the amount of P is not particularly limited, but is usually about 0.001%.
- S 0.02% or less (excluding 0%) S, like P, is an element that degrades the toughness and ductility of steel. In order to prevent disconnection in the wire drawing or the subsequent twisting process, the S content is set to 0.02% or less.
- the amount of S is preferably 0.01% or less, and more preferably 0.005% or less.
- the lower limit of the amount of S is not particularly limited, but is usually about 0.001%.
- N 0.005% or less (excluding 0%)
- N is an element that deteriorates the ductility of steel when the content is excessive. Therefore, the N amount is set to 0.005% or less.
- the amount of N is preferably 0.004% or less, and more preferably 0.003% or less.
- the lower limit of the N amount is not particularly limited, but is usually about 0.001%.
- the basic components of the steel wire rod of the present invention are as described above, and the balance is substantially iron. However, it is naturally allowed that the inevitable impurities brought in depending on the situation of raw materials, materials, manufacturing facilities, etc. are included in the steel wire. Furthermore, it is also recommended to add the following elements as necessary within a range not impeding the effects of the present invention.
- Cr 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%) Cr and Ni are both elements that increase the hardenability of steel and contribute to the improvement of strength.
- the Cr content is preferably 0.05% or more, and the Ni content is preferably 0.03% or more. More preferably, the Cr amount and the Ni amount are both 0.10% or more, and more preferably both are 0.12% or more.
- the Cr content and the Ni content are both 0.3% or less. More preferably, the Cr content and the Ni content are both 0.25% or less, more preferably 0.20% or less.
- Cu 0.2% or less (excluding 0%) Cu is an element having an action of promoting scale peeling.
- the amount of Cu is preferably 0.01% or more.
- the amount of Cu is more preferably 0.05% or more, and further preferably 0.10% or more.
- the amount of Cu becomes excessive, peeling of the scale is excessively promoted, the scale is peeled off during rolling, and another thin scale with high adhesion is generated on the peeled surface, and the wire coil is stored and transported. Rust is generated when Therefore, the amount of Cu is preferably 0.2% or less.
- the amount of Cu is more preferably 0.17% or less, and still more preferably 0.15% or less.
- Nb, V, Ti, Hf, and Zr are all elements that form fine carbonitrides and contribute to high strength.
- the Nb amount, the V amount, the Ti amount, the Hf amount, and the Zr amount are all 0.003% or more.
- the Nb amount, V amount, Ti amount, Hf amount, and Zr amount are all preferably 0.007% or more, and more preferably 0.01% or more.
- the total amount of these elements is preferably 0.1% or less.
- the total amount of these elements is more preferably 0.08% or less, still more preferably 0.06% or less.
- Al 0.1% or less (excluding 0%) Al is an element effective as a deoxidizer.
- the Al content is preferably 0.001% or more.
- the amount of Al is more preferably 0.005% or more, and still more preferably 0.01% or more.
- the Al content is preferably 0.1% or less.
- the amount of Al is more preferably 0.08% or less, and still more preferably 0.06% or less.
- B 0.005% or less (excluding 0%)
- B is an element that suppresses the formation of ferrite by being present as free B that dissolves in steel (B that does not form a compound), and is particularly effective for high-strength wires that require suppression of longitudinal cracks. It is.
- the B content is preferably 0.0001% or more.
- the amount of B is more preferably 0.0005% or more, and further preferably 0.0010% or more.
- the B content is preferably 0.005% or less, more preferably 0.0040% or less, and still more preferably 0.0035% or less.
- Ca and Mg are both elements that have the effect of increasing the ductility by controlling the form of inclusions. Moreover, Ca also has the effect
- both the Ca content and the Mg content are preferably 0.001% or more.
- Ca and Mg are both preferably 0.002% or more, and more preferably 0.003% or more.
- both the Ca content and the Mg content are preferably 0.01% or less.
- the Ca content and the Mg content are both preferably 0.008% or less, and more preferably 0.005% or less.
- the obtained steel wire was measured by the following method.
- No. 3, 29, 33, 36, 40, 43, 46, 47, and 49 have deteriorated MD properties because the manufacturing conditions do not satisfy the requirements of the present invention.
- No. 3, 29, 36, 40, 43, 46, and 47 are examples in which air was blown and cooled after hot rolling, and FeO became Fe 3 O 4 during cooling, so that the FeO fraction was It could not be secured, and the MD property deteriorated.
- No. No. 33 is an example in which the coiling temperature after hot rolling was high. The scale thickness was increased, the FeO ratio was too large, and the Fe 2 SiO 4 ratio was also high, so the MD property deteriorated.
- No. Nos. 50 to 54 are examples in which the coiling temperature after hot rolling was higher, the scale thickness exceeded 7.0 ⁇ m, the scale peeling rate of the rolled material increased, and rust was generated. That is, no. Nos. 50 to 54 are considered to cause rust due to dropping of the scale during cooling after hot rolling or during storage and transportation.
- FIG. 2 shows the relationship between the scale thickness and the scale peeling rate of the rolled material. It can be seen that when the scale thickness exceeds 7.0 ⁇ m, the scale peeling rate of the rolled material increases.
- the steel wire rod of the present invention is excellent in mechanical descaling after hot rolling (before wire drawing), it cuts automobile tire cords (steel cords, bead wires), hose wires, semiconductor silicon, etc. It is useful as a material such as saw wire used in
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Abstract
Description
Cは、鋼の機械的性質に大きく影響する元素である。線材の強度を確保するため、C量を0.05%以上と定めた。C量は好ましくは0.15%以上であり、より好ましくは0.3%以上である。一方、C量が過剰になると、線材製造時の熱間加工性が劣化する。そこでC量を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1.0%以下である。 C: 0.05 to 1.2%
C is an element that greatly affects the mechanical properties of steel. In order to ensure the strength of the wire, the C content was set to 0.05% or more. The amount of C is preferably 0.15% or more, and more preferably 0.3% or more. On the other hand, when the amount of C becomes excessive, hot workability at the time of manufacturing the wire is deteriorated. Therefore, the C amount is set to 1.2% or less. The amount of C is preferably 1.1% or less, and more preferably 1.0% or less.
Siは、鋼の脱酸のために必要な元素であり、その含有量が少なすぎると、Fe2SiO4(ファイアライト)の生成が不十分となって、MD性が劣化する。そこで、Si量を0.01%以上と定めた。Si量は、好ましくは0.1%以上であり、より好ましくは0.2%以上である。一方、Si量が過剰になると、Fe2SiO4(ファイアライト)の過剰生成によって、MD性が著しく劣化する他、表面脱炭層が生成するなどの問題が生じる。そこで、Si量を0.5%以下と定めた。Si量は、好ましくは0.45%以下であり、より好ましくは0.4%以下である。 Si: 0.01 to 0.5%
Si is an element necessary for deoxidation of steel, and if its content is too small, the production of Fe 2 SiO 4 (firelight) becomes insufficient and the MD property deteriorates. Therefore, the Si amount is determined to be 0.01% or more. The amount of Si is preferably 0.1% or more, and more preferably 0.2% or more. On the other hand, when the amount of Si is excessive, problems such as excessive degradation of Fe 2 SiO 4 (firelite) cause significant deterioration of MD properties and formation of a surface decarburized layer. Therefore, the Si amount is set to 0.5% or less. The amount of Si is preferably 0.45% or less, and more preferably 0.4% or less.
Mnは、鋼の焼入れ性を確保し、強度を高めるのに有用な元素である。このような作用を有効に発揮させるため、Mn量を0.1%以上と定めた。Mn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、Mn量が過剰になると、熱間圧延後の冷却過程で偏析を起こし、伸線加工性等に有害な過冷組織(マルテンサイト等)が発生しやすくなる。そこでMn量を1.5%以下と定めた。Mn量は、好ましくは1.4%以下であり、より好ましくは1.2%以下である。 Mn: 0.1 to 1.5%
Mn is an element useful for securing the hardenability of steel and increasing the strength. In order to effectively exhibit such an action, the amount of Mn was determined to be 0.1% or more. The amount of Mn is preferably 0.2% or more, and more preferably 0.4% or more. On the other hand, when the amount of Mn is excessive, segregation occurs in the cooling process after hot rolling, and a supercooled structure (such as martensite) that is harmful to wire drawing workability is likely to occur. Therefore, the amount of Mn is set to 1.5% or less. The amount of Mn is preferably 1.4% or less, more preferably 1.2% or less.
Pは、鋼の靭性及び延性を劣化させる元素である。伸線工程等における断線を防止するため、P量を0.02%以下と定めた。P量は好ましくは0.01%以下であり、より好ましくは0.005%以下である。P量の下限は特に限定されないが、通常0.001%程度である。 P: 0.02% or less (excluding 0%)
P is an element that deteriorates the toughness and ductility of steel. In order to prevent disconnection in the wire drawing process or the like, the P content is set to 0.02% or less. The amount of P is preferably 0.01% or less, and more preferably 0.005% or less. The lower limit of the amount of P is not particularly limited, but is usually about 0.001%.
Sは、Pと同様に、鋼の靭性及び延性を劣化させる元素である。伸線やその後の撚り工程における断線を防止するため、S量を0.02%以下と定めた。S量は、好ましくは0.01%以下であり、より好ましくは0.005%以下である。S量の下限は特に限定されないが、通常、0.001%程度である。 S: 0.02% or less (excluding 0%)
S, like P, is an element that degrades the toughness and ductility of steel. In order to prevent disconnection in the wire drawing or the subsequent twisting process, the S content is set to 0.02% or less. The amount of S is preferably 0.01% or less, and more preferably 0.005% or less. The lower limit of the amount of S is not particularly limited, but is usually about 0.001%.
Nは、含有量が過剰になると、鋼の延性を劣化させる元素である。そこで、N量を0.005%以下と定めた。N量は、好ましくは0.004%以下であり、より好ましくは0.003%以下である。N量の下限は特に限定されないが、通常、0.001%程度である。 N: 0.005% or less (excluding 0%)
N is an element that deteriorates the ductility of steel when the content is excessive. Therefore, the N amount is set to 0.005% or less. The amount of N is preferably 0.004% or less, and more preferably 0.003% or less. The lower limit of the N amount is not particularly limited, but is usually about 0.001%.
Cr及びNiは、いずれも鋼の焼入れ性を高めて、強度の向上に寄与する元素である。このような作用を有効に発揮させるためCr量は0.05%以上であることが好ましく、Ni量は0.03%以上であることが好ましい。より好ましいCr量、Ni量はいずれも0.10%以上であり、さらに好ましくはいずれも0.12%以上である。一方、Cr量及びNi量が過剰になると、マルテンサイト組織が発生しやすくなる上、スケールの地鉄との密着性が高まり過ぎて、MD時のスケールの剥離性が劣化する。そこで、Cr量、Ni量はいずれも0.3%以下であるのが好ましい。より好ましいCr量、Ni量はいずれも0.25%以下であり、さらに好ましくはいずれも0.20%以下である。 Cr: 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%)
Cr and Ni are both elements that increase the hardenability of steel and contribute to the improvement of strength. In order to effectively exhibit such an action, the Cr content is preferably 0.05% or more, and the Ni content is preferably 0.03% or more. More preferably, the Cr amount and the Ni amount are both 0.10% or more, and more preferably both are 0.12% or more. On the other hand, when the amount of Cr and the amount of Ni are excessive, a martensite structure is likely to be generated, and the adhesion of the scale to the ground iron is excessively increased, so that the peelability of the scale during MD deteriorates. Therefore, it is preferable that the Cr content and the Ni content are both 0.3% or less. More preferably, the Cr content and the Ni content are both 0.25% or less, more preferably 0.20% or less.
Cuは、スケール剥離を促進する作用を有する元素である。このような作用を有効に発揮させるため、Cu量は0.01%以上であることが好ましい。Cu量は、より好ましくは0.05%以上であり、さらに好ましくは0.10%以上である。一方、Cu量が過剰になると、スケールの剥離が過剰に促進され、圧延中にスケールが剥離してその剥離面に薄くて密着性の高い別のスケールが発生する他、線材コイルを保管・搬送する際に錆が発生する。そこで、Cu量は0.2%以下であることが好ましい。Cu量は、より好ましくは0.17%以下であり、さらに好ましくは0.15%以下である。 Cu: 0.2% or less (excluding 0%)
Cu is an element having an action of promoting scale peeling. In order to effectively exhibit such an action, the amount of Cu is preferably 0.01% or more. The amount of Cu is more preferably 0.05% or more, and further preferably 0.10% or more. On the other hand, when the amount of Cu becomes excessive, peeling of the scale is excessively promoted, the scale is peeled off during rolling, and another thin scale with high adhesion is generated on the peeled surface, and the wire coil is stored and transported. Rust is generated when Therefore, the amount of Cu is preferably 0.2% or less. The amount of Cu is more preferably 0.17% or less, and still more preferably 0.15% or less.
Nb、V、Ti、Hf、及びZrは、いずれも微細な炭窒化物を形成して、高強度化に寄与する元素である。このような作用を有効に発揮させるため、Nb量、V量、Ti量、Hf量、及びZr量はいずれも、0.003%以上であることが好ましい。Nb量、V量、Ti量、Hf量、及びZr量はいずれも、より好ましくは0.007%以上であり、さらに好ましくは0.01%以上である。一方、これらの元素が過剰なると、延性が劣化するため、これらの合計量は0.1%以下であることが好ましい。これら元素の合計量は、より好ましくは0.08%以下であり、さらに好ましくは0.06%以下である。 A total of at least one element selected from the group consisting of Nb, V, Ti, Hf, and Zr is 0.1% or less (excluding 0%)
Nb, V, Ti, Hf, and Zr are all elements that form fine carbonitrides and contribute to high strength. In order to effectively exhibit such an action, it is preferable that the Nb amount, the V amount, the Ti amount, the Hf amount, and the Zr amount are all 0.003% or more. The Nb amount, V amount, Ti amount, Hf amount, and Zr amount are all preferably 0.007% or more, and more preferably 0.01% or more. On the other hand, if these elements are excessive, the ductility deteriorates, so the total amount of these elements is preferably 0.1% or less. The total amount of these elements is more preferably 0.08% or less, still more preferably 0.06% or less.
Alは、脱酸剤として有効な元素である。このような作用を有効に発揮させるため、Al量は0.001%以上であることが好ましい。Al量は、より好ましくは0.005%以上であり、さらに好ましくは0.01%以上である。一方、Al量が過剰になると、Al2O3等の酸化物系介在物が多くなり、伸線加工時などに断線が多発する。そこで、Al量は0.1%以下であることが好ましい。Al量は、より好ましくは0.08%以下であり、さらに好ましくは0.06%以下である。 Al: 0.1% or less (excluding 0%)
Al is an element effective as a deoxidizer. In order to effectively exhibit such an action, the Al content is preferably 0.001% or more. The amount of Al is more preferably 0.005% or more, and still more preferably 0.01% or more. On the other hand, when the amount of Al becomes excessive, oxide inclusions such as Al 2 O 3 increase, and disconnection frequently occurs during wire drawing. Therefore, the Al content is preferably 0.1% or less. The amount of Al is more preferably 0.08% or less, and still more preferably 0.06% or less.
Bは、鋼中に固溶するフリーなB(化合物を形成しないB)として存在することにより、フェライトの生成を抑制する元素であり、特に縦割れの抑制が必要な高強度線材で有効な元素である。このような作用を有効に発揮させるため、B量は0.0001%以上であることが好ましい。B量は、より好ましくは0.0005%以上であり、さらに好ましくは0.0010%以上である。一方、B量が過剰になると、延性が劣化する。そこでB量は、0.005%以下であることが好ましく、より好ましくは0.0040%以下であり、さらに好ましくは0.0035%以下である。 B: 0.005% or less (excluding 0%)
B is an element that suppresses the formation of ferrite by being present as free B that dissolves in steel (B that does not form a compound), and is particularly effective for high-strength wires that require suppression of longitudinal cracks. It is. In order to effectively exhibit such an action, the B content is preferably 0.0001% or more. The amount of B is more preferably 0.0005% or more, and further preferably 0.0010% or more. On the other hand, when the amount of B becomes excessive, ductility deteriorates. Therefore, the B content is preferably 0.005% or less, more preferably 0.0040% or less, and still more preferably 0.0035% or less.
CaとMgは、いずれも介在物の形態を制御して、延性を高める作用を有する元素である。また、Caは鋼材の耐食性を高める作用も有する。このような作用を有効に発揮させるため、Ca量及びMg量はいずれも0.001%以上であることが好ましい。Ca及びMgは、いずれも0.002%以上であることがより好ましく、さらに好ましくは0.003%以上である。一方、これらの元素が過剰になると、加工性が劣化する。そこで、Ca量、Mg量は、いずれも0.01%以下であることが好ましい。Ca量、Mg量は、いずれも0.008%以下であることがより好ましく、0.005%以下であることがさらに好ましい。 Ca: 0.01% or less (not including 0%) and / or Mg: 0.01% or less (not including 0%)
Ca and Mg are both elements that have the effect of increasing the ductility by controlling the form of inclusions. Moreover, Ca also has the effect | action which improves the corrosion resistance of steel materials. In order to effectively exhibit such an action, both the Ca content and the Mg content are preferably 0.001% or more. Ca and Mg are both preferably 0.002% or more, and more preferably 0.003% or more. On the other hand, when these elements are excessive, workability deteriorates. Therefore, both the Ca content and the Mg content are preferably 0.01% or less. The Ca content and the Mg content are both preferably 0.008% or less, and more preferably 0.005% or less.
コイルの前端、中央部、後端のそれぞれから、長さ10mmのサンプルを採取し、各々のサンプルから任意の3箇所のスケール断面を走査型電子顕微鏡(SEM)で観察した(観察倍率:5000倍)。各測定箇所について、鋼線材周方向長さ100μmで10点スケール厚さを測定して、そのスケール平均厚さを求め、3箇所の平均値を各サンプルのスケール厚さとした。さらに各サンプル(コイル前端、中央部、後端)の平均値を算出して、各試験No.のスケール厚さとした。 (1) Measurement of scale thickness Samples with a length of 10 mm were taken from each of the front end, center portion, and rear end of the coil, and arbitrary three scale sections were taken from each sample with a scanning electron microscope (SEM). Observed (observation magnification: 5000 times). About each measurement location, 10-point scale thickness was measured by the steel wire material circumferential direction length of 100 micrometers, the scale average thickness was calculated | required, and the average value of 3 locations was made into the scale thickness of each sample. Furthermore, the average value of each sample (coil front end, center part, rear end) was calculated, and each test No. And the scale thickness.
上記(1)と同様に、コイルの前端、中央部、後端のそれぞれから、長さ10mmのサンプルを採取し、各々のサンプルから任意の3箇所のスケール断面について、X線回折を行い、FeO、Fe2SiO4、Fe2O3、及びFe3O4のピーク強度比から、FeO及びFe2SiO4の比率(体積%)を求めた。3箇所の平均値を、各サンプルのFeO比率及びFe2SiO4比率とした。さらに各サンプル(コイル前端、中央部、後端)の平均値を算出して、各試験No.のFeO比率及びFe2SiO4比率とした。 (2) Measurement of scale composition
Similarly to the above (1), samples having a length of 10 mm are taken from the front end, the central portion, and the rear end of the coil, and X-ray diffraction is performed on any three scale sections from each sample, and FeO From the peak intensity ratio of Fe 2 SiO 4 , Fe 2 O 3 , and Fe 3 O 4 , the ratio (volume%) of FeO and Fe 2 SiO 4 was determined. The average value of three, and the FeO ratio and Fe 2 SiO 4 ratio of each sample. Furthermore, the average value of each sample (coil front end, center part, rear end) was calculated, and each test No. FeO ratio and Fe 2 SiO 4 ratio.
コイルの前端、中央部、後端のそれぞれから、長さ200mmのサンプルを採取し、サンプルに風を吹きかけて鋼線材表面のスケールを吹き飛ばした。デジタルカメラによって、風を吹きかける前後の外観を写真撮影し、画像解析で両者を比較することによって、剥離したスケールの面積率を求めた。 (3) Measurement of scale peelability of rolled material
A sample having a length of 200 mm was taken from each of the front end, center portion, and rear end of the coil, and the sample was blown to blow off the scale on the surface of the steel wire. The appearance of the wind before and after blowing was photographed with a digital camera, and the area ratio of the peeled scale was determined by comparing the two with image analysis.
コイルの前端、中央部、後端のそれぞれから、長さ250mmのサンプルを採取し、引張試験機で6%の変形歪を与えて、チャックから取り出した後、サンプルに風を吹きかけて鋼線材表面のスケールを吹き飛ばした。デジタルカメラによって、歪付与前後の外観を写真撮影し、画像解析で両者を比較することによって残留スケール面積率を算出した。 (4) MD measurement
Samples with a length of 250 mm were taken from the front end, center, and rear end of the coil, subjected to 6% deformation strain with a tensile tester, taken out from the chuck, and then air blown over the sample to surface the steel wire Blowed off the scale. The external appearance before and after applying the distortion was photographed with a digital camera, and the residual scale area ratio was calculated by comparing the two by image analysis.
No.3、29、36、40、43、46、47は、熱間圧延後、大気を噴きつけて冷却した例であり、冷却中にFeOがFe3O4となったことによって、FeO分率が確保できず、MD性が劣化した。No.33は、熱間圧延後の巻取り温度が高かった例であり、スケール厚さが厚くなるとともに、FeO比率が大きくなりすぎ、さらにFe2SiO4比率も高かったため、MD性が劣化した。No.49は、熱間圧延後の巻取り温度が低かった例であり、FeO比率が確保できず、MD性が劣化した。No.50~54は、熱間圧延後の巻取り温度がさらに高かった例であり、スケール厚さが7.0μmを超え、圧延材のスケール剥離率が上昇し、錆が発生していた。すなわち、No.50~54は熱間圧延後の冷却中や保管・搬送時にスケールが脱落して、錆が発生するものと考えられる。 On the other hand, no. 3, 29, 33, 36, 40, 43, 46, 47, and 49 have deteriorated MD properties because the manufacturing conditions do not satisfy the requirements of the present invention.
No. 3, 29, 36, 40, 43, 46, and 47 are examples in which air was blown and cooled after hot rolling, and FeO became Fe 3 O 4 during cooling, so that the FeO fraction was It could not be secured, and the MD property deteriorated. No. No. 33 is an example in which the coiling temperature after hot rolling was high. The scale thickness was increased, the FeO ratio was too large, and the Fe 2 SiO 4 ratio was also high, so the MD property deteriorated. No. No. 49 is an example in which the coiling temperature after hot rolling was low, the FeO ratio could not be ensured, and the MD property deteriorated. No. Nos. 50 to 54 are examples in which the coiling temperature after hot rolling was higher, the scale thickness exceeded 7.0 μm, the scale peeling rate of the rolled material increased, and rust was generated. That is, no. Nos. 50 to 54 are considered to cause rust due to dropping of the scale during cooling after hot rolling or during storage and transportation.
本出願は、2011年1月7日出願の日本特許出願(特願2011-002014に基づくものであり、その内容はここに参照として取り込まれる。 Although the present invention has been described in detail and with reference to specific embodiments, it will be apparent to those skilled in the art that various changes and modifications can be made without departing from the spirit and scope of the invention.
This application is based on a Japanese patent application filed on Jan. 7, 2011 (Japanese Patent Application No. 2011-002014), the contents of which are incorporated herein by reference.
Claims (4)
- C :0.05~1.2%(質量%の意味。以下、化学成分について同じ。)、
Si:0.01~0.5%、
Mn:0.1~1.5%、
P :0.02%以下(0%を含まない)、
S :0.02%以下(0%を含まない)、
N :0.005%以下(0%を含まない)を含有し、残部が鉄及び不可避不純物である鋼線材であって、
厚さ7.0μm以下のスケールを有し、且つ、該スケール中のFeO比率が30~80体積%であり、Fe2SiO4比率が0.1体積%未満であることを特徴とする鋼線材。 C: 0.05 to 1.2% (meaning mass%, hereinafter the same for chemical components),
Si: 0.01 to 0.5%,
Mn: 0.1 to 1.5%
P: 0.02% or less (excluding 0%),
S: 0.02% or less (excluding 0%),
N: a steel wire containing 0.005% or less (excluding 0%), the balance being iron and inevitable impurities,
A steel wire having a scale with a thickness of 7.0 μm or less, an FeO ratio in the scale of 30 to 80% by volume, and an Fe 2 SiO 4 ratio of less than 0.1% by volume . - 更に、下記(1)~(6)の少なくとも1つを含有する請求項1に記載の鋼線材。
(1)Cr:0.3%以下(0%を含まない)及び/又はNi:0.3%以下(0%を含まない)
(2)Cu:0.2%以下(0%を含まない)
(3)Nb、V、Ti、Hf、及びZrよりなる群から選択される少なくとも1種の元素を、合計で0.1%以下(0%を含まない)
(4)Al:0.1%以下(0%を含まない)
(5)B:0.005%以下(0%を含まない)
(6)Ca:0.01%以下(0%を含まない)及び/又はMg:0.01%以下(0%を含まない) The steel wire according to claim 1, further comprising at least one of the following (1) to (6).
(1) Cr: 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%)
(2) Cu: 0.2% or less (excluding 0%)
(3) A total of at least one element selected from the group consisting of Nb, V, Ti, Hf, and Zr is 0.1% or less (excluding 0%)
(4) Al: 0.1% or less (excluding 0%)
(5) B: 0.005% or less (excluding 0%)
(6) Ca: 0.01% or less (not including 0%) and / or Mg: 0.01% or less (not including 0%) - 請求項1または2に記載の化学成分の鋼を、
熱間圧延後、750~880℃で巻取り、
酸素分率が20体積%未満である酸素と不活性ガスとの混合ガス、又は不活性ガスを噴きつけながら冷却することを特徴とする鋼線材の製造方法。 The chemical component steel according to claim 1 or 2,
After hot rolling, it is wound at 750-880 ° C,
A method for producing a steel wire material, characterized by cooling while spraying a mixed gas of oxygen and an inert gas having an oxygen fraction of less than 20% by volume, or an inert gas. - 前記不活性ガスが窒素である請求項3に記載の製造方法。 The manufacturing method according to claim 3, wherein the inert gas is nitrogen.
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP12732406.9A EP2662468A4 (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for producing same |
US13/995,739 US20130272914A1 (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for manufacturing same |
CN201280004664.4A CN103314125B (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for producing same |
KR1020147014715A KR20140076642A (en) | 2011-01-07 | 2012-01-06 | Method for producing steel wire material |
KR1020137017580A KR20130087613A (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for producing same |
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JP2011-002014 | 2011-01-07 | ||
JP2011002014A JP4980471B1 (en) | 2011-01-07 | 2011-01-07 | Steel wire rod and manufacturing method thereof |
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WO2012093715A1 true WO2012093715A1 (en) | 2012-07-12 |
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PCT/JP2012/050155 WO2012093715A1 (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for producing same |
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US (1) | US20130272914A1 (en) |
EP (1) | EP2662468A4 (en) |
JP (1) | JP4980471B1 (en) |
KR (2) | KR20140076642A (en) |
CN (1) | CN103314125B (en) |
WO (1) | WO2012093715A1 (en) |
Cited By (1)
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WO2018194038A1 (en) * | 2017-04-17 | 2018-10-25 | 株式会社ブリヂストン | Cable bead and airplane tire using same |
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BR112017020004A2 (en) * | 2015-04-08 | 2018-06-19 | Nippon Steel & Sumitomo Metal Corporation | steel sheet for heat treatment |
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KR101676201B1 (en) * | 2015-12-07 | 2016-11-15 | 주식회사 포스코 | High carbon steel wire rod and steel wire having excellent hydrogen induced cracking resistance and method for manufacturing thereof |
JP6757194B2 (en) * | 2016-07-11 | 2020-09-16 | 日本パーカライジング株式会社 | Pre-heat treatment carbon steel with excellent scale removal properties, post-heat treatment carbon steel and their manufacturing methods, scale removal methods and easily descalable film forming agents |
CN110546324B (en) | 2017-04-28 | 2022-02-18 | 株式会社普利司通 | Steel cord for reinforcing rubber article, method for producing same, and tire |
WO2020065372A1 (en) * | 2018-09-25 | 2020-04-02 | Arcelormittal | High strength hot rolled steel having excellent scale adhesivness and a method of manufacturing the same |
EP3674425B1 (en) * | 2018-12-31 | 2022-05-04 | Baker Hughes Energy Technology UK Limited | Steel wire |
CN110560495A (en) * | 2019-09-17 | 2019-12-13 | 安徽工业大学 | Laboratory scale removal experiment platform and experiment method thereof |
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Also Published As
Publication number | Publication date |
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KR20130087613A (en) | 2013-08-06 |
JP2012144756A (en) | 2012-08-02 |
KR20140076642A (en) | 2014-06-20 |
JP4980471B1 (en) | 2012-07-18 |
CN103314125B (en) | 2015-05-27 |
CN103314125A (en) | 2013-09-18 |
EP2662468A1 (en) | 2013-11-13 |
EP2662468A4 (en) | 2015-05-27 |
US20130272914A1 (en) | 2013-10-17 |
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