WO2013146676A1 - 線材及びこれを用いた鋼線 - Google Patents
線材及びこれを用いた鋼線 Download PDFInfo
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- WO2013146676A1 WO2013146676A1 PCT/JP2013/058566 JP2013058566W WO2013146676A1 WO 2013146676 A1 WO2013146676 A1 WO 2013146676A1 JP 2013058566 W JP2013058566 W JP 2013058566W WO 2013146676 A1 WO2013146676 A1 WO 2013146676A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- 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
Definitions
- 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.
- PC prestressed concrete
- 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.
- JIS G3536 for example, 7 strands of ⁇ 15.2mm
- the one having a maximum test force of about 261 kN is known.
- 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.
- 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 is spheroidized by performing blueing at a temperature of 450 ° C. or higher after wire drawing, A technique for improving delayed fracture resistance is disclosed.
- 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.
- Patent Document 2 discloses a technique for improving delayed fracture resistance by using a processed pearlite structure in which a compressive residual stress is applied to the surface layer of a PC steel wire having a carbon content of 0.6 to 1.3%. ing.
- 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.
- Patent Document 3 discloses that in a bearing steel having a carbon content of 0.65 to 1.20%, 50 to 300 nm of Ti-based or Al-based nitride or the like is dispersed for a predetermined amount or more to trap hydrogen.
- a technique for improving delayed fracture resistance in a tempered martensite structure is disclosed.
- 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.
- 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.
- 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.
- 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 ⁇ m was also selected from AlN. We found that it is important to secure the above.
- the wire 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 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.) More than 95 area% of the structure is a pearlite structure, the AlN amount is 0.005% or more, and the diameter d of AlN expressed by the geometric mean (ab) 1/2 of the length a and the thickness b In the maximum value extreme value distribution of GM , the ratio of AlN having d GM of 10 to 20 ⁇ m is
- 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.
- the present invention also includes a steel wire obtained from the above wire.
- 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 ⁇ m) are appropriately present.
- Wire can be provided.
- the twist characteristic of a steel wire can be improved by adjusting the amount of solute N below predetermined.
- the amount of AlN is set to 0.005% or more because the hydrogen trap effect increases as the amount increases.
- 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%.
- the maximum value extreme value distribution is used as an index for securing the number of AlN having a size of 10 to 20 ⁇ m.
- a geometric average (ab) 1/2 of the length a and the thickness b of AlN is used, and this is expressed as d GM ( ⁇ m).
- d GM ⁇ m
- the length “a” of AlN means the length of AlN in the longitudinal direction of the wire
- the thickness “b” of AlN means the length of AlN in the direction perpendicular to the longitudinal direction of the wire.
- 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) It means the thing which statistically processed about.
- the ratio of AlN having d GM (max) of 10 to 20 ⁇ m is set to 50% or more on the number basis.
- the ratio of AlN having d GM (max) of 10 to 20 ⁇ m is set to 50% or more on the number basis.
- 95% by area or more of the main phase structure is a pearlite structure.
- the area ratio of the pearlite structure is preferably 97% or more, and more preferably 100%.
- C 0.8-1.2% 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.
- 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 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.
- Si 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.
- 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 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.
- 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.
- 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 to 0.010%
- the amount of N is preferably 0.0025% or more, more preferably 0.0030% or more (particularly 0.0040% or more).
- 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.
- 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% and [Al] ⁇ ⁇ 2.1 ⁇ 10 ⁇ [N] +0.255
- 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.
- 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.
- the upper limit of the Al amount is set to 0.15% and satisfies the relationship of the following formula (1).
- 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.
- 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% 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% 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.
- the basic components of the wire rod 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.
- 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.
- 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 is an element that increases the toughness of the steel wire after wire drawing.
- the Ni content is preferably 0.05% or more, more preferably 0.1% or more, and further preferably 0.2% or more.
- the Ni content is preferably 1.0% or less, more preferably 0.7% or less, and still more preferably 0.6% or less.
- Co has the effect of reducing proeutectoid cementite (especially when the amount of C is high) and making it easy to control the structure to a uniform pearlite structure.
- the Co content is preferably 0.05% or more, more preferably 0.1% or more, and further preferably 0.2% or more.
- the Co content is preferably 1.0% or less, more preferably 0.8% or less, and still more preferably 0.6% or less.
- Mo is an element that improves the corrosion resistance of steel wires.
- the Mo amount is preferably 0.05% or more, more preferably 0.1% or more.
- the Mo amount is preferably 1.0% or less, more preferably 0.5% or less, and still more preferably 0.3% or less.
- Cu is an element that improves the corrosion resistance of steel wires.
- the amount of Cu is preferably 0.05% or more, more preferably 0.08% or more.
- the amount of Cu 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.
- the amount of Cu is preferably 0.5% or less, more preferably 0.2% or less, and further preferably 0.18% or less.
- 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.
- the amount of B is preferably 0.0003% or more, more preferably 0.0005% or more, and further preferably 0.001% or more.
- a Fe—B compound for example, FeB 2
- 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 forms an excessive solid solution N and nitride after AlN is precipitated and contributes to refinement of crystal grains, and also has an effect of suppressing aging embrittlement by fixing the solid solution N.
- the Nb content is preferably 0.01% or more, more preferably 0.03% or more, and still more preferably 0.05% or more.
- the Nb amount is preferably 0.5% or less, more preferably 0.4% or less, and still more preferably 0.2%. % Or less.
- V like Nb, forms excess solid solution N and nitride after AlN is precipitated and contributes to refinement of crystal grains, and also has an effect of suppressing aging embrittlement by fixing solid solution N.
- the V amount is preferably 0.01% or more, more preferably 0.02% or more, and further preferably 0.03% or more.
- the amount of V is preferably 0.5% or less, more preferably 0.4% or less, and still more preferably 0.2%. % Or less.
- Wire rods are usually obtained by melting, split-rolling, and hot-rolling (and patenting as necessary) steel with appropriately controlled chemical components.
- AlN starts to precipitate in steel at about 1300 ° C. or less, 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.
- the heating temperature in the batch rolling is set to 1230 to 1280 ° C.
- 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.
- 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.
- 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).
- the billet obtained by the block rolling is hot-rolled, then cooled to 850 to 950 ° C. by water cooling or the like, and placed in a coil shape.
- the mounting temperature is preferably 850 ° C. or higher, more preferably 870 ° C. or higher, and further preferably 890 ° C. or higher.
- the reheating temperature during the patenting treatment is preferably 880 to 1000 ° C.
- the patenting temperature is preferably 530 to 620 ° C.
- the precipitation amount can be increased by setting the reheating temperature lower (for example, about 880 to 940 ° C.).
- 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.
- wire rod of the present invention sufficiently secures AlN that can effectively act as a hydrogen trap site, steel wires such as wire rope and PC steel wire using this have excellent delayed fracture resistance and are useful. It is.
- the present invention also includes such a steel wire.
- the 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 be processed 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. The results are shown in Table 2.
- 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 maximum AlN size was measured in the field of view and this was done for any 20 fields of view.
- 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.
- the obtained wire coil was drawn to produce a steel wire, and the tensile strength (strand strength) of the steel wire was measured. Furthermore, twisted wire processing and hot stretch treatment were performed to form a twisted wire having a twisted wire diameter and a twisted wire structure as shown in Table 2, and the rope strength, delayed fracture resistance, and twisting properties of the twisted wire were measured. . The results are shown in Table 3.
- Rope strength was measured according to JIS G3536 by measuring the maximum test force of a tensile test.
- Delayed Fracture Resistance are 0.8 p.p. based on the description in Reference 1 (fib Bulletin No. 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.
- test no. Nos. 4, 6 to 8, 11, 12, 21 to 27 are examples in which any of the requirements of the present invention was not satisfied or the manufacturing conditions necessary for obtaining the steel material of the present invention were not satisfied. is there.
- 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. No. 11 caused a burning crack because the heating temperature at the time of the block rolling was too high.
- No. No. 12 had a patenting treatment temperature that was too low, resulting in a mixed structure (P + B) of bainite (B) and pearlite (P), and the drawability was reduced.
- the fraction of bainite was about 20 area%.
- 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. 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. 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. 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.
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
[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95面積%以上がパーライト組織であるとともに、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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
鋼線の引張強度を、JIS Z2241に従って測定した。
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。
遅れ破壊特性は、文献1(fib Bulletin No.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。
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。
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95面積%以上がパーライト組織であるとともに、
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線材。 - 固溶N量が0.003%以下である請求項1に記載の線材。
- 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に記載の線材。 - 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に記載の線材。 - 請求項1~4のいずれかに記載の線材から得られる鋼線。
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20180216208A1 (en) * | 2015-07-21 | 2018-08-02 | Nippon Steel & Sumitomo Metal Corporation | High-strength pc steel wire |
US20180216213A1 (en) * | 2015-07-21 | 2018-08-02 | Nippon Steel & Sumitomo Metal Corporation | High-strength pc steel wire |
AU2018245893B2 (en) * | 2017-03-31 | 2021-10-07 | Nippon Steel Corporation | Railway wheel |
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KR102117400B1 (ko) * | 2018-08-31 | 2020-06-01 | 주식회사 포스코 | 냉간압조용 선재, 이를 이용한 가공품 및 이들의 제조방법 |
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Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2004131797A (ja) | 2002-10-10 | 2004-04-30 | Nippon Steel Corp | 耐遅れ破壊特性の良好なpc鋼線およびその製造方法ならびにpc撚り線 |
JP3591236B2 (ja) | 1997-09-04 | 2004-11-17 | 日本精工株式会社 | 転がり軸受 |
JP2004360005A (ja) | 2003-06-04 | 2004-12-24 | Nippon Steel Corp | 遅れ破壊特性の優れた高強度pc鋼線およびその製造方法 |
WO2007001057A1 (ja) * | 2005-06-29 | 2007-01-04 | Nippon Steel Corporation | 伸線特性に優れた高強度線材およびその製造方法 |
JP2008261027A (ja) * | 2007-04-13 | 2008-10-30 | Nippon Steel Corp | 耐水素脆化特性に優れた高強度亜鉛めっきボルト及びその製造方法 |
JP2009280836A (ja) * | 2008-05-19 | 2009-12-03 | Nippon Steel Corp | 耐遅れ破壊特性に優れた高強度pc鋼線及びその製造方法 |
WO2011089782A1 (ja) * | 2010-01-25 | 2011-07-28 | 新日本製鐵株式会社 | 線材、鋼線、及び線材の製造方法 |
JP2012041587A (ja) * | 2010-08-17 | 2012-03-01 | Nippon Steel Corp | 高強度かつ耐水素脆化特性に優れた機械部品用線材、鋼線、および機械部品とその製造方法 |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60149732A (ja) * | 1984-01-13 | 1985-08-07 | Sumitomo Electric Ind Ltd | 鋼線材の熱処理方法 |
JPS61261430A (ja) * | 1985-05-14 | 1986-11-19 | Shinko Kosen Kogyo Kk | 高強度高靭性鋼線の製造方法 |
JPH05171267A (ja) * | 1991-09-27 | 1993-07-09 | Nippon Steel Corp | 高靭性パーライト鋼の製造法 |
US20070187003A1 (en) * | 2004-03-02 | 2007-08-16 | Honda Motor Co., Ltd. | High-strength bolt superior in delayed fracture and resistance and relaxation resistance |
CN101208445B (zh) * | 2005-06-29 | 2014-11-26 | 新日铁住金株式会社 | 拉丝性能优异的高强度线材及其制造方法 |
JP5169839B2 (ja) * | 2007-01-31 | 2013-03-27 | 新日鐵住金株式会社 | 捻回特性に優れるpws用めっき鋼線及びその製造方法 |
CN102137949B (zh) * | 2009-06-25 | 2013-09-11 | 新日铁住金株式会社 | 耐蚀性和疲劳特性优良的桥梁用高强度Zn-Al镀层钢丝及其制造方法 |
BR112012025089A2 (pt) * | 2010-04-01 | 2017-09-12 | Kobe Steel Ltd | Fio de aço de alto carbono excelente na estampabilidade de fio e propriedade de fadiga após trefilagem do fio |
-
2012
- 2012-03-29 JP JP2012077003A patent/JP5802162B2/ja not_active Expired - Fee Related
-
2013
- 2013-03-25 EP EP13767810.8A patent/EP2832878B1/en active Active
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- 2013-03-25 WO PCT/JP2013/058566 patent/WO2013146676A1/ja active Application Filing
- 2013-03-25 ES ES13767810T patent/ES2743735T3/es active Active
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-
2014
- 2014-09-19 ZA ZA2014/06891A patent/ZA201406891B/en unknown
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3591236B2 (ja) | 1997-09-04 | 2004-11-17 | 日本精工株式会社 | 転がり軸受 |
JP2004131797A (ja) | 2002-10-10 | 2004-04-30 | Nippon Steel Corp | 耐遅れ破壊特性の良好なpc鋼線およびその製造方法ならびにpc撚り線 |
JP2004360005A (ja) | 2003-06-04 | 2004-12-24 | Nippon Steel Corp | 遅れ破壊特性の優れた高強度pc鋼線およびその製造方法 |
WO2007001057A1 (ja) * | 2005-06-29 | 2007-01-04 | Nippon Steel Corporation | 伸線特性に優れた高強度線材およびその製造方法 |
JP2008261027A (ja) * | 2007-04-13 | 2008-10-30 | Nippon Steel Corp | 耐水素脆化特性に優れた高強度亜鉛めっきボルト及びその製造方法 |
JP2009280836A (ja) * | 2008-05-19 | 2009-12-03 | Nippon Steel Corp | 耐遅れ破壊特性に優れた高強度pc鋼線及びその製造方法 |
WO2011089782A1 (ja) * | 2010-01-25 | 2011-07-28 | 新日本製鐵株式会社 | 線材、鋼線、及び線材の製造方法 |
JP2012041587A (ja) * | 2010-08-17 | 2012-03-01 | Nippon Steel Corp | 高強度かつ耐水素脆化特性に優れた機械部品用線材、鋼線、および機械部品とその製造方法 |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20180216208A1 (en) * | 2015-07-21 | 2018-08-02 | Nippon Steel & Sumitomo Metal Corporation | High-strength pc steel wire |
US20180216213A1 (en) * | 2015-07-21 | 2018-08-02 | Nippon Steel & Sumitomo Metal Corporation | High-strength pc steel wire |
US10752974B2 (en) * | 2015-07-21 | 2020-08-25 | Nippon Steel Corporation | High-strength PC steel wire |
US10808305B2 (en) * | 2015-07-21 | 2020-10-20 | Nippon Steel Corporation | High-strength PC steel wire |
AU2018245893B2 (en) * | 2017-03-31 | 2021-10-07 | Nippon Steel Corporation | Railway wheel |
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EP2832878A4 (en) | 2016-04-27 |
EP2832878A1 (en) | 2015-02-04 |
KR101624447B1 (ko) | 2016-05-25 |
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ZA201406891B (en) | 2016-01-27 |
MX2014011471A (es) | 2014-12-08 |
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