WO2017170439A1 - Steel wire having excellent delayed fracture resistance - Google Patents
Steel wire having excellent delayed fracture resistance Download PDFInfo
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- WO2017170439A1 WO2017170439A1 PCT/JP2017/012461 JP2017012461W WO2017170439A1 WO 2017170439 A1 WO2017170439 A1 WO 2017170439A1 JP 2017012461 W JP2017012461 W JP 2017012461W WO 2017170439 A1 WO2017170439 A1 WO 2017170439A1
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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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
- 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
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
Definitions
- the present invention relates to a steel wire excellent in delayed fracture resistance.
- high carbon steel wires such as PC steel wires are known to have delayed fracture resistance superior to tempered martensite structure materials.
- the delayed fracture resistance is deteriorated even with a high carbon steel wire, and the risk of delayed fracture increases.
- Patent Document 1 discloses a PC steel wire excellent in delayed fracture resistance with a limited amount of compressive residual stress applied to the surface layer portion
- Patent Document 2 includes a steel cord having a microstructure in which cementite is finely divided.
- a high-strength steel wire rod for use, Patent Document 3, discloses a bainite PC steel rod having a ⁇ 110> texture.
- JP 2004-131797 A Japanese Patent Laid-Open No. 11-269607 JP-A-7-268545
- Patent Document 1 The PC steel wire disclosed in Patent Document 1 is certainly excellent in delayed fracture resistance. However, when the local corrosion occurs and the inside of the surface layer having the compressive residue on the surface becomes a stress concentrated portion, it is assumed that sufficient delayed fracture resistance cannot be obtained.
- the high-strength steel wire rod disclosed in Patent Document 2 has high strength after the final wire drawing and does not cause vertical cracks in the torsion test. Therefore, it is suitable for ultra-fine steel cords. However, it is difficult to use for large civil engineering and building structures.
- An object of the present invention is to provide a steel wire excellent in delayed fracture resistance (particularly a steel wire excellent in delayed fracture resistance even in an environment where local corrosion occurs).
- the present invention has been made to solve the above-mentioned problems, and the gist of the present invention is a steel wire having the following delayed fracture resistance.
- the chemical composition is mass%, C: 0.60 to 1.1% Si: 0.05 to 1.5%, Mn: 0.30 to 1.5%, P: 0.030% or less, S: 0.030% or less, Al: 0.005 to 0.05%, N: 0.001 to 0.006%, Cr: 0 to 1.5%, Ti: 0 to 0.02%, B: 0 to 0.005%,
- the metal structure is made of pearlite, and in a cross section perpendicular to the longitudinal direction, the orientation degree of the ⁇ 110 ⁇ crystal plane of the bcc phase is 0.95 or more,
- the wire diameter is 2.9 mm or more, Steel wire with excellent delayed fracture resistance.
- the chemical composition is mass%, Ti: 0.003-0.02%, and B: 0.0005 to 0.005%, Containing one or more selected from A steel wire excellent in delayed fracture resistance according to (1) or (2) above.
- a steel wire having a tensile fracture strength of 2000 MPa or more and excellent delayed fracture resistance can be obtained.
- a steel wire whose microstructure is pearlite has a degree of orientation of the ⁇ 110 ⁇ crystal plane of the bcc phase (hereinafter, simply referred to as “degree of orientation of ⁇ 110 ⁇ crystal plane”) in a cross section perpendicular to the longitudinal direction. ) Is 0.95 or more, the delayed fracture resistance is remarkably improved.
- C 0.60 to 1.1% C is an essential element for securing the strength of the drawn pearlite steel wire.
- the C content is less than 0.60%, the amount of pro-eutectoid ferrite increases even when kept in a suitable temperature range of 650 to 550 ° C., which will be described later, and therefore the required strength (tensile strength of 2000 MPa or more) is achieved. I can't get it.
- the C content exceeds 1.1%, the amount of pro-eutectoid cementite increases and the wire drawing characteristics are remarkably deteriorated, and a suitable cold wire drawing with a total true strain of 2.3 or more described later is performed. Can not be applied. Therefore, the C content is set to 0.60 to 1.1%.
- the preferable lower limit of the C content is 0.80%, and the preferable upper limit is 1.0%.
- Si 0.05 to 1.5%
- Si has an effect of increasing strength by solid solution strengthening, and is an effective element for obtaining strength. If the Si content is less than 0.05%, the above effect cannot be exhibited. On the other hand, when the Si content is too large, precipitation of pro-eutectoid ferrite is promoted, and the limit working degree in wire drawing is reduced, and a suitable cold wire drawing with a total true strain of 2.3 or more described later is preferable. Cannot be applied. Therefore, the Si content is set to 0.05 to 1.5%.
- the preferable lower limit of the Si content is 0.10%, and the preferable upper limit is 1.0%.
- Mn 0.30 to 1.5%
- Mn is an element necessary not only for deoxidation and desulfurization, but also for stably forming lamellae and obtaining a tensile strength of 2000 MPa or more in the pearlite transformation treatment. If the content of Mn is less than 0.30%, the above effect cannot be obtained. On the other hand, even if the content exceeds 1.5%, an effect commensurate with the amount cannot be obtained. Therefore, the Mn content is set to 0.30 to 1.5%.
- the minimum with preferable Mn content is 0.40%, and a preferable upper limit is 0.90%.
- P 0.030% or less
- P is contained as an impurity, and segregates at a grain boundary to deteriorate delayed fracture resistance. For this reason, content of P shall be 0.030% or less.
- the content of P is preferably as low as possible.
- S 0.030% or less S is contained as an impurity and segregates at the grain boundary to deteriorate the delayed fracture resistance. For this reason, content of S shall be 0.030% or less.
- the S content is preferably as low as possible.
- Al 0.005 to 0.05%
- Al is an element effective as a deoxidizer, and has an effect of making austenite grains finer by forming nitrides.
- the Al content is 0.005 to 0.05%.
- the preferable lower limit of the Al content is 0.02%, and the preferable upper limit is 0.04%.
- Al content of this invention points out content in total Al.
- N 0.001 to 0.006% N has an effect of making the austenite grains fine by generating Al nitride. If the N content is less than 0.001%, this effect is insufficient. On the other hand, if the N content exceeds 0.006%, cold wire workability deteriorates. Therefore, the N content is set to 0.001 to 0.006%. The minimum with preferable N content is 0.002%, and a preferable upper limit is 0.005%.
- Cr 0 to 1.5% Cr is an element effective for reducing the lamella spacing of pearlite and improving the strength. For this reason, you may contain Cr as needed. However, if the content of Cr is too large, the transformation end time becomes long, and even if kept in a suitable temperature range of 650 to 550 ° C. described later, the pearlite transformation is not completed and martensite may be generated. Therefore, the upper limit of the Cr content when contained is 1.5%.
- the upper limit of the Cr content is preferably 0.60%.
- the minimum of Cr content is 0.10%.
- Ti 0 to 0.02%
- Ti is a deoxidizing element and has an effect of fixing solid solution N and improving wire drawing workability. For this reason, you may contain Ti as needed. However, if the Ti content exceeds 0.02%, the effect may be saturated and a coarse oxide may be formed to deteriorate the cold drawing workability. Therefore, the upper limit of the Ti content when contained is 0.02%. In addition, in order to acquire the said effect stably, it is preferable that the minimum of Ti content is 0.003%.
- B 0 to 0.005%
- B has the effect of suppressing the formation of proeutectoid ferrite and increasing the tensile strength after pearlite transformation. For this reason, you may contain B as needed. However, the above effect is saturated even if B is contained in excess of 0.005%. Therefore, the upper limit of the B content when contained is 0.005%. In addition, in order to acquire the said effect stably, it is preferable that the minimum of B content is 0.0005%.
- the balance is Fe and impurities.
- impurities are components mixed in due to various factors in raw materials such as ores and scraps and manufacturing processes when industrially producing steel materials, and are permitted within a range that does not adversely affect the present invention. Means what will be done.
- the metal structure of the steel wire according to the present invention is made of pearlite, and the degree of orientation of the ⁇ 110 ⁇ crystal plane of the bcc phase is 0.95 or more in a cross section perpendicular to the longitudinal direction. For this reason, as shown in the Examples described later, it is possible to achieve both a high strength of 2000 MPa or more in tensile strength and excellent delayed fracture resistance. A preferable lower limit of the degree of orientation is 0.97. On the other hand, in the case of a steel wire having a final wire diameter of 2.9 mm or more, about 0.99 is the upper limit of the degree of orientation.
- pro-eutectoid ferrite or pro-eutectoid cementite alone is 5% or less, or both pro-eutectoid ferrite and pro-eutectoid cementite are 5% or less in total. As long as it is within the range, it may be included.
- the integrated intensity “P 0 ” of the (110) plane and (hkl) plane of the phase is a value in a non-oriented sample.
- (110), (200), and (211) are used as crystal planes, and data on non-oriented samples are described in a powder X-ray diffraction database (PDF (Powder Diffraction File)).
- PDF Powder X-ray diffraction Database
- the structure of the steel wire of the present invention is pearlite.
- Pearlite is one in which a ferrite phase and a cementite phase form a layered structure. Therefore, the orientation degree of the ⁇ 110 ⁇ crystal plane of the bcc phase is substantially the orientation degree of the ⁇ 110 ⁇ crystal plane of the ferrite constituting the pearlite.
- a small amount of pro-eutectoid ferrite of 5% or less may be contained.
- the orientation degree of the ⁇ 110 ⁇ crystal plane of the ferrite constituting the pearlite and the orientation degree of the ⁇ 110 ⁇ crystal plane of the pro-eutectoid ferrite cannot be obtained separately. Therefore, it is determined not by the orientation degree of the ⁇ 110 ⁇ crystal plane of the ferrite constituting the pearlite but by the orientation degree of the ⁇ 110 ⁇ crystal plane of the bcc phase.
- the wire diameter of the steel wire according to the present invention (final wire diameter of the steel wire) is 2.9 mm or more. This is because the PC steel wire corrodes due to the cracking of the concrete in the case of PC steel wire, etc., especially when the wire diameter is smaller than 2.9 mm, it is not a delayed failure but a failure due to corrosion. This is because the lifetime may be shortened.
- the wire diameter is preferably 3.0 mm or more. Although there is no particular limitation on the wire diameter, an industrial upper limit of 7 mm is appropriate.
- (D) Manufacturing method The steel wire of this invention can be suitably manufactured by the method shown below, for example. The method is not limited to this method.
- the low alloy steel having the chemical composition described in the above section (A) After melting the low alloy steel having the chemical composition described in the above section (A), it is cast into an ingot or slab. Next, the cast ingot or slab is subjected to hot working such as hot rolling and hot forging to produce a steel slab, and the steel slab is rolled to obtain a steel bar or wire having a circular cross section. Finish. Thereafter, the steel bar or the wire may be drawn into a steel wire by an appropriate method as necessary. Steps (i) to (iv) described below are sequentially performed on the steel bar, the wire, and the steel wire (hereinafter collectively referred to as “round steel”) having a circular cross section. Thus, the steel wire excellent in delayed fracture resistance of the present invention is produced. In addition, you may perform the aging treatment of a process (v) after a process (iv).
- a preferred upper limit of the austenitizing temperature is 1000 ° C., and a more preferred upper limit is 950 ° C.
- said austenitization temperature points out the temperature in the surface of a round steel material.
- the austenitizing time is set to 5 to 30 minutes.
- the preferable lower limit of the austenitizing time is 10 minutes, and the preferable upper limit is 20 minutes.
- Cooling rate of the round steel material austenitized in step (i) Is cooled to a temperature range of 650 to 550 ° C. at a rate of 1 ° C./second or more, and held in the temperature range for 1 to 30 minutes to make the metal structure fine pearlite.
- the cooling rate after austenitization is less than 1 ° C / sec, pearlite transformation starts before reaching the above holding temperature range, resulting in a coarse pearlite structure, so cracks occur during cold drawing. There is a case.
- the upper limit of the cooling rate after austenitization is about 200 ° C./second industrially.
- the holding time in the temperature range of 650 to 550 ° C. is less than 1 minute, the pearlite transformation may not be completed due to the influence of the size of the round steel material and / or contained elements, but on the other hand, it takes a long time exceeding 30 minutes However, the manufacturing cost increases.
- the preferable lower limit of the holding time is 3 minutes, and the preferable upper limit is 10 minutes.
- the cooling rate in step (ii) refers to the average cooling rate on the surface of the round steel material.
- the temperature range to be cooled and held refers to the set temperature of an isothermal transformation treatment facility with good heat conduction, such as a salt bath or a lead bath.
- the chemical composition described in the above section (A) is included.
- the round steel material which performed the process from the said process (i) to the process (iii) in order is cold-drawn.
- the total true strain by cold drawing is set to 2.3 or more.
- the preferable lower limit of the total true strain of the cold wire drawing is 2.5, and the preferable upper limit is 3.0.
- the number of cold drawing processes is not particularly limited, and may be one or more.
- the cold wire drawing in step (iv) needs to be performed without softening the round steel material cooled to room temperature in step (iii).
- the round steel material cooled to room temperature may be subjected to descaling treatment by pickling or the like before cold drawing, if necessary.
- descaling treatment by pickling or the like before cold drawing, if necessary.
- the aging treatment may be performed by heating for 2 to 30 minutes. This is because if the heating temperature of the aging treatment is less than 200 ° C., the effect cannot be obtained sufficiently, and if it exceeds 450 ° C., the tensile strength is greatly reduced. Furthermore, if the holding time in the temperature range of 200 to 450 ° C. is less than 10 seconds, the effect cannot be sufficiently obtained, and even if the holding time exceeds 30 minutes, the effect is saturated and only the production cost is increased. It is.
- the above aging temperature refers to the surface temperature of the steel wire.
- the cooling in the aging treatment is preferably carried out in the air.
- Ingots obtained by melting steels A to R having the chemical composition shown in Table 1 and casting them into molds were heated to 1250 ° C., and were made into round steel materials (wires) having a diameter of 20 mm by hot forging.
- Steels A to L and Steels N to R in Table 1 are steels whose chemical compositions are within the range defined by the present invention.
- the steel M is a steel whose chemical composition deviates from the conditions specified in the present invention.
- the wire rod (round steel material) having a diameter of 20 mm obtained as described above was pickled with hydrochloric acid at room temperature, subjected to a phosphate coating treatment, and then pre-drawn to obtain steel wires having the diameters shown in Table 2 (round steel material). ).
- each steel wire obtained by the preliminary wire drawing is heated to the temperature shown in Table 2 for 10 minutes to form austenite, and then held in a lead bath at the temperature shown in Table 2 for 1 minute to perform transformation treatment. It was. At that time, a thermocouple was attached to the steel wire, and the cooling rate was measured. The cooling rate from the heating temperature of the steel wire to the transformation temperature (lead bath temperature) was 7 to 60 ° C./second. In addition, it cooled with water after the transformation process.
- the steel wire after cooling is then pickled with hydrochloric acid at room temperature, subjected to phosphate coating treatment, and then cold drawn to the final wire diameter under the conditions shown in Table 2 without softening treatment in the middle. Went.
- Some steel wires were subjected to an “aging treatment” in which after wire drawing, the steel was further heated in the air at the temperature shown in Table 2 for 5 minutes and allowed to cool.
- Delayed fracture resistance For the test numbers for which a tensile strength of 1700 MPa or more was obtained in the investigation of ⁇ 2> above, a notch having a depth of 0.5 mm, an angle of 60 °, and a notch bottom radius of 0.1 mm was formed on each steel wire of the final wire diameter. Using the provided test specimen, the delayed fracture resistance was investigated by the following method.
- FIG. 1 shows the delayed fracture resistance characteristics of each steel wire by comparing the delayed fracture strength ratio and the tensile strength on the vertical axis and the horizontal axis, respectively.
- test numbers 1 to 25 of the present invention are superior in both tensile strength and delayed fracture resistance compared to the test numbers 26 to 29 of the comparative example.
- the chemical compositions of the steel A and the steel B used are both within the range defined by the present invention, but the orientation degree of the ⁇ 110 ⁇ crystal plane of the bcc phase is 0.76. It is inferior in both tensile strength and delayed fracture resistance as compared with the examples of the present invention, because it is as small as ⁇ 0.92 and deviates from the conditions specified in the present invention.
- Test No. 29 of the comparative example has a C content of the steel M used as low as 0.38% and is out of the conditions specified in the present invention. Therefore, the tensile strength is only 1458 MPa, which is extremely inferior to the present invention example. ing.
- the steel wire excellent in delayed fracture resistance of the present invention has a tensile strength of 2000 MPa or more and is excellent in delayed fracture resistance even in an environment where local corrosion occurs. Therefore, it is possible to increase the size of civil engineering and building structures. Can also respond. For this reason, the present invention has a remarkable industrial contribution.
Abstract
Description
C:0.60~1.1%、
Si:0.05~1.5%、
Mn:0.30~1.5%、
P:0.030%以下、
S:0.030%以下、
Al:0.005~0.05%、
N:0.001~0.006%、
Cr:0~1.5%、
Ti:0~0.02%、
B:0~0.005%、
残部:Feおよび不純物からなり、
金属組織が、パーライトからなりかつ、長手方向に垂直な断面において、bcc相の{110}結晶面の配向度が0.95以上であり、
線径が、2.9mm以上である、
耐遅れ破壊特性に優れた鋼線。 (1) The chemical composition is mass%,
C: 0.60 to 1.1%
Si: 0.05 to 1.5%,
Mn: 0.30 to 1.5%,
P: 0.030% or less,
S: 0.030% or less,
Al: 0.005 to 0.05%,
N: 0.001 to 0.006%,
Cr: 0 to 1.5%,
Ti: 0 to 0.02%,
B: 0 to 0.005%,
The balance: Fe and impurities,
The metal structure is made of pearlite, and in a cross section perpendicular to the longitudinal direction, the orientation degree of the {110} crystal plane of the bcc phase is 0.95 or more,
The wire diameter is 2.9 mm or more,
Steel wire with excellent delayed fracture resistance.
Cr:0.10~1.5%を含有する、
上記(1)に記載の耐遅れ破壊特性に優れた鋼線。 (2) The chemical composition is mass%,
Containing Cr: 0.10 to 1.5%,
A steel wire having excellent delayed fracture resistance as described in (1) above.
Ti:0.003~0.02%、および、
B:0.0005~0.005%、
から選択される1種以上を含有する、
上記(1)または(2)に記載の耐遅れ破壊特性に優れた鋼線。 (3) The chemical composition is mass%,
Ti: 0.003-0.02%, and
B: 0.0005 to 0.005%,
Containing one or more selected from
A steel wire excellent in delayed fracture resistance according to (1) or (2) above.
本発明に係る鋼線の化学組成の限定理由は次の通りである。以下の説明において各元素の含有量の「%」は「質量%」を意味する。 (A) Chemical composition:
The reasons for limiting the chemical composition of the steel wire according to the present invention are as follows. In the following description, “%” of the content of each element means “mass%”.
Cは、伸線加工パーライト鋼線の強度を確保する上で必須の元素である。Cの含有量が0.60%未満では、たとえ後述の650~550℃という好適な温度範囲に保持した場合でも初析フェライト量が増大するため、所要の強度(引張強さで2000MPa以上)が得られない。一方、Cの含有量が1.1%を超えると、初析セメンタイト量が増加して伸線加工特性が著しく劣化し、後述の総真ひずみ2.3以上という好適な冷間伸線加工を施すことができない。そのため、Cの含有量は0.60~1.1%とする。C含有量の好ましい下限は0.80%であり、また、好ましい上限は1.0%である。 C: 0.60 to 1.1%
C is an essential element for securing the strength of the drawn pearlite steel wire. When the C content is less than 0.60%, the amount of pro-eutectoid ferrite increases even when kept in a suitable temperature range of 650 to 550 ° C., which will be described later, and therefore the required strength (tensile strength of 2000 MPa or more) is achieved. I can't get it. On the other hand, if the C content exceeds 1.1%, the amount of pro-eutectoid cementite increases and the wire drawing characteristics are remarkably deteriorated, and a suitable cold wire drawing with a total true strain of 2.3 or more described later is performed. Can not be applied. Therefore, the C content is set to 0.60 to 1.1%. The preferable lower limit of the C content is 0.80%, and the preferable upper limit is 1.0%.
Siは、固溶強化によって強度を高める効果があり、強度を得るために有効な元素である。Siの含有量が0.05%未満では前記効果が発揮できない。一方、Siの含有量が多すぎると、初析フェライトの析出を促進するとともに、伸線加工での限界加工度が低下し、後述の総真ひずみ2.3以上という好適な冷間伸線加工を施すことができない。このため、Siの含有量は0.05~1.5%とする。Si含有量の好ましい下限は0.10%であり、また、好ましい上限は1.0%である。 Si: 0.05 to 1.5%
Si has an effect of increasing strength by solid solution strengthening, and is an effective element for obtaining strength. If the Si content is less than 0.05%, the above effect cannot be exhibited. On the other hand, when the Si content is too large, precipitation of pro-eutectoid ferrite is promoted, and the limit working degree in wire drawing is reduced, and a suitable cold wire drawing with a total true strain of 2.3 or more described later is preferable. Cannot be applied. Therefore, the Si content is set to 0.05 to 1.5%. The preferable lower limit of the Si content is 0.10%, and the preferable upper limit is 1.0%.
Mnは、脱酸、脱硫のために必要であるばかりでなく、パーライト変態処理において安定的にラメラを形成し、2000MPa以上の引張強さを得るために必要な元素である。Mnの含有量が0.30%未満では上記の効果が得られず、一方、1.5%を超えて含有させてもその量に見合う効果が得られない。このため、Mnの含有量は0.30~1.5%とする。Mn含有量の好ましい下限は0.40%であり、また、好ましい上限は0.90%である。 Mn: 0.30 to 1.5%
Mn is an element necessary not only for deoxidation and desulfurization, but also for stably forming lamellae and obtaining a tensile strength of 2000 MPa or more in the pearlite transformation treatment. If the content of Mn is less than 0.30%, the above effect cannot be obtained. On the other hand, even if the content exceeds 1.5%, an effect commensurate with the amount cannot be obtained. Therefore, the Mn content is set to 0.30 to 1.5%. The minimum with preferable Mn content is 0.40%, and a preferable upper limit is 0.90%.
Pは、不純物として含有され、結晶粒界に偏析して耐遅れ破壊特性を劣化させる。このため、Pの含有量は0.030%以下とする。Pの含有量は極力低いことが好ましい。 P: 0.030% or less P is contained as an impurity, and segregates at a grain boundary to deteriorate delayed fracture resistance. For this reason, content of P shall be 0.030% or less. The content of P is preferably as low as possible.
Sは、不純物として含有され、結晶粒界に偏析して耐遅れ破壊特性を劣化させる。このため、Sの含有量は0.030%以下とする。Sの含有量は極力低いことが好ましい。 S: 0.030% or less S is contained as an impurity and segregates at the grain boundary to deteriorate the delayed fracture resistance. For this reason, content of S shall be 0.030% or less. The S content is preferably as low as possible.
Alは、脱酸剤として有効な元素であり、また、窒化物を生成することにより、オーステナイト粒を細粒化させる効果がある。しかし、Alの含有量が0.005%未満では、これらの効果が不十分であり、0.05%を超えて含有させても効果が飽和する。このため、Alの含有量は0.005~0.05%とする。Al含有量の好ましい下限は0.02%であり、また、好ましい上限は0.04%である。なお、本発明のAl含有量とはトータルAlでの含有量を指す。 Al: 0.005 to 0.05%
Al is an element effective as a deoxidizer, and has an effect of making austenite grains finer by forming nitrides. However, if the Al content is less than 0.005%, these effects are insufficient, and even if the content exceeds 0.05%, the effects are saturated. Therefore, the Al content is 0.005 to 0.05%. The preferable lower limit of the Al content is 0.02%, and the preferable upper limit is 0.04%. In addition, Al content of this invention points out content in total Al.
Nは、Alの窒化物を生成することにより、オーステナイト粒を細粒化させる効果がある。Nの含有量が0.001%未満であるとこの効果が不十分であり、一方、0.006%を超えると冷間伸線加工性が低下する。このため、N含有量は0.001~0.006%とする。N含有量の好ましい下限は0.002%であり、また、好ましい上限は0.005%である。 N: 0.001 to 0.006%
N has an effect of making the austenite grains fine by generating Al nitride. If the N content is less than 0.001%, this effect is insufficient. On the other hand, if the N content exceeds 0.006%, cold wire workability deteriorates. Therefore, the N content is set to 0.001 to 0.006%. The minimum with preferable N content is 0.002%, and a preferable upper limit is 0.005%.
Crは、パーライトのラメラ間隔を微細化し、強度を向上させるのに有効な元素である。このため、必要に応じてCrを含有させてもよい。しかしながら、Crの含有量が多過ぎると、変態終了時間が長くなり、たとえ後述の650~550℃という好適な温度範囲に保持した場合でもパーライト変態が完了せず、マルテンサイトが生じる恐れがある。したがって、含有させる場合のCr含有量の上限を1.5%とする。Cr含有量の上限は、0.60%であることが好ましい。なお、前記の効果を安定して得るためには、Cr含有量の下限は、0.10%であることが好ましい。 Cr: 0 to 1.5%
Cr is an element effective for reducing the lamella spacing of pearlite and improving the strength. For this reason, you may contain Cr as needed. However, if the content of Cr is too large, the transformation end time becomes long, and even if kept in a suitable temperature range of 650 to 550 ° C. described later, the pearlite transformation is not completed and martensite may be generated. Therefore, the upper limit of the Cr content when contained is 1.5%. The upper limit of the Cr content is preferably 0.60%. In addition, in order to acquire the said effect stably, it is preferable that the minimum of Cr content is 0.10%.
Tiは、脱酸元素であり、固溶Nを固定して伸線加工性を向上させる効果を有する。このため、必要に応じてTiを含有させてもよい。しかしながら、Tiの含有量が0.02%を超えると、効果が飽和するとともに粗大な酸化物を形成して冷間伸線加工性を劣化させることがある。したがって、含有させる場合のTi含有量の上限を0.02%とする。なお、前記の効果を安定して得るためには、Ti含有量の下限は、0.003%であることが好ましい。 Ti: 0 to 0.02%
Ti is a deoxidizing element and has an effect of fixing solid solution N and improving wire drawing workability. For this reason, you may contain Ti as needed. However, if the Ti content exceeds 0.02%, the effect may be saturated and a coarse oxide may be formed to deteriorate the cold drawing workability. Therefore, the upper limit of the Ti content when contained is 0.02%. In addition, in order to acquire the said effect stably, it is preferable that the minimum of Ti content is 0.003%.
Bは、初析フェライトの生成を抑制し、パーライト変態後の引張強さを高める効果を有する。このため、必要に応じてBを含有させてもよい。しかしながら、Bを0.005%を超えて含有させても、上記効果が飽和する。したがって、含有させる場合のB含有量の上限を0.005%とする。なお、前記の効果を安定して得るためには、B含有量の下限は、0.0005%であることが好ましい。 B: 0 to 0.005%
B has the effect of suppressing the formation of proeutectoid ferrite and increasing the tensile strength after pearlite transformation. For this reason, you may contain B as needed. However, the above effect is saturated even if B is contained in excess of 0.005%. Therefore, the upper limit of the B content when contained is 0.005%. In addition, in order to acquire the said effect stably, it is preferable that the minimum of B content is 0.0005%.
本発明に係る鋼線の金属組織は、パーライトからなり、かつ、長手方向に垂直な断面において、bcc相の{110}結晶面の配向度が0.95以上である。このため、後述の実施例に示すように、引張強さで2000MPa以上の高強度と優れた耐遅れ破壊特性との両立が達成できる。上記配向度の好ましい下限は0.97である。一方、最終線径が2.9mm以上の鋼線の場合は、0.99程度が上記配向度の上限になる。なお、パーライトからなる本発明に係る鋼線の金属組織には面積率で、初析フェライトもしくは初析セメンタイトを単独で5%以下、または初析フェライトと初析セメンタイトの双方を合計で5%以下、の範囲であれば含んでもよい。 (B) Metal structure:
The metal structure of the steel wire according to the present invention is made of pearlite, and the degree of orientation of the {110} crystal plane of the bcc phase is 0.95 or more in a cross section perpendicular to the longitudinal direction. For this reason, as shown in the Examples described later, it is possible to achieve both a high strength of 2000 MPa or more in tensile strength and excellent delayed fracture resistance. A preferable lower limit of the degree of orientation is 0.97. On the other hand, in the case of a steel wire having a final wire diameter of 2.9 mm or more, about 0.99 is the upper limit of the degree of orientation. In addition, in the metal structure of the steel wire according to the present invention made of pearlite, by area ratio, pro-eutectoid ferrite or pro-eutectoid cementite alone is 5% or less, or both pro-eutectoid ferrite and pro-eutectoid cementite are 5% or less in total. As long as it is within the range, it may be included.
F=(P-P0)/(1-P0)
P=ΣI(110)/ΣI(hkl)
なお、上記の2式において、「F」はbcc相の{110}結晶面の配向度、「I(110)」および「I(hkl)」は、伸線加工方向に垂直な横断面におけるbcc相の(110)面および(hkl)面の積分強度、「P0」は無配向試料における値である。後述の実施例では、結晶面は(110)、(200)および(211)を採用し、また、無配向試料のデータは粉末X線回折のデータベース(PDF(Powder Diffraction File))に記載されている強度の数値を使用した。 The degree of orientation of the {110} crystal plane of the bcc phase is determined by performing X-ray diffraction on a cross section perpendicular to the longitudinal direction of the steel wire (transverse cross section perpendicular to the wire drawing direction) to obtain the integrated strength of each crystal plane. Calculate with the following formula.
F = (P−P 0 ) / (1−P 0 )
P = ΣI (110) / ΣI (hkl)
In the above two formulas, “F” is the degree of orientation of the {110} crystal plane of the bcc phase, and “I (110)” and “I (hkl)” are bcc in a cross section perpendicular to the wire drawing direction. The integrated intensity “P 0 ” of the (110) plane and (hkl) plane of the phase is a value in a non-oriented sample. In examples described later, (110), (200), and (211) are used as crystal planes, and data on non-oriented samples are described in a powder X-ray diffraction database (PDF (Powder Diffraction File)). The strength value used is used.
本発明に係る鋼線の線径(鋼線の最終線径)は2.9mm以上である。これは、PC鋼線等ではコンクリートのき裂発生によりPC鋼線が腐食して、特に、線径が2.9mm未満の細径の場合には、遅れ破壊ではなく、腐食による破断を原因として寿命が短くなることがあるからである。該線径は、3.0mm以上であることが好ましい。線径には特に制限はないものの、工業的な上限は7mmが妥当である。 (C) Wire diameter:
The wire diameter of the steel wire according to the present invention (final wire diameter of the steel wire) is 2.9 mm or more. This is because the PC steel wire corrodes due to the cracking of the concrete in the case of PC steel wire, etc., especially when the wire diameter is smaller than 2.9 mm, it is not a delayed failure but a failure due to corrosion. This is because the lifetime may be shortened. The wire diameter is preferably 3.0 mm or more. Although there is no particular limitation on the wire diameter, an industrial upper limit of 7 mm is appropriate.
本発明の鋼線は、例えば、以下に示す方法によって、好適に製造することができる。なお、この方法に限られるものでない。 (D) Manufacturing method:
The steel wire of this invention can be suitably manufactured by the method shown below, for example. The method is not limited to this method.
オーステナイト化温度が850℃未満では、オーステナイト化が不十分なことがある。一方、オーステナイト化温度が1050℃を超えると、オーステナイト粒の粗大化が起きて伸線加工性が低下し、工程(iv)の総真ひずみ2.3以上という冷間伸線加工を施すことができない場合がある。このため、オーステナイト化温度を850~1050℃とする。オーステナイト化温度の下限は、900℃とすることが好ましい。オーステナイト粒の細粒化の観点から、オーステナイト化温度の好ましい上限は1000℃であり、より好ましい上限は950℃である。なお、上記のオーステナイト化温度は、丸鋼材の表面における温度を指す。 Step (i): Step of heating to 850 to 1050 ° C. for 5 to 30 minutes to form austenite If the austenitizing temperature is less than 850 ° C., austenitizing may be insufficient. On the other hand, when the austenitizing temperature exceeds 1050 ° C., the austenite grains become coarse and the wire drawing workability deteriorates, and the cold wire drawing with a total true strain of 2.3 or more in the step (iv) is performed. There are cases where it is not possible. For this reason, the austenitizing temperature is set to 850 to 1050 ° C. The lower limit of the austenitizing temperature is preferably 900 ° C. From the viewpoint of austenite grain refinement, a preferred upper limit of the austenitizing temperature is 1000 ° C., and a more preferred upper limit is 950 ° C. In addition, said austenitization temperature points out the temperature in the surface of a round steel material.
工程(i)でオーステナイト化した丸鋼材を、冷却速度を1℃/秒以上として、650~550℃の温度範囲まで急冷し、該温度範囲で1~30分保持して、金属組織を微細なパーライトにする。オーステナイト化後の冷却速度が1℃/秒未満の場合には、上記の保持温度範囲に達する前にパーライト変態が開始して、粗大なパーライト組織となるため、冷間伸線加工時にクラックが発生する場合がある。さらに、上記温度範囲での保持によるパーライト変態の開始前に初析フェライトが析出したり初析セメンタイトが析出したりして、引張強さで2000MPa以上の高強度と優れた耐遅れ破壊特性との両立が達成できない場合もある。なお、オーステナイト化後の冷却速度の上限は工業的には200℃/秒程度である。 Step (ii): Step of cooling to a temperature range of 650 to 550 ° C. at a cooling rate of 1 ° C./second or more, and maintaining the temperature range for 1 to 30 minutes. Cooling rate of the round steel material austenitized in step (i) Is cooled to a temperature range of 650 to 550 ° C. at a rate of 1 ° C./second or more, and held in the temperature range for 1 to 30 minutes to make the metal structure fine pearlite. When the cooling rate after austenitization is less than 1 ° C / sec, pearlite transformation starts before reaching the above holding temperature range, resulting in a coarse pearlite structure, so cracks occur during cold drawing. There is a case. Furthermore, pro-eutectoid ferrite precipitates or pro-eutectoid cementite precipitates before the start of pearlite transformation by holding in the above temperature range, and high tensile strength of 2000 MPa or more and excellent delayed fracture resistance In some cases, it is impossible to achieve both. The upper limit of the cooling rate after austenitization is about 200 ° C./second industrially.
上記工程(ii)の処理を終了させた後、丸鋼材は室温まで冷却される。この際の冷却速度については、特に制限がない。 Step (iii): Step of cooling to room temperature After finishing the process of step (ii), the round steel material is cooled to room temperature. There is no particular limitation on the cooling rate at this time.
前記(A)項で述べた化学組成を有し、上記工程(i)から工程(iii)までの工程を順に施した丸鋼材は、冷間伸線加工する。特に、冷間伸線加工による総真ひずみを2.3以上とすることにより、引張強さで2000MPa以上の高強度を具えることができ、bcc相の{110}結晶面の配向度を0.95以上とすることができる。このため、冷間伸線加工による総真ひずみを2.3以上とする。冷間伸線加工の総真ひずみの好ましい下限は2.5であり、また、好ましい上限は3.0である。総真ひずみが2.3以上であれば、冷間伸線加工の回数は特に限定されず、1回でも複数回でもよい。ただし、工程(iv)における冷間伸線加工は、工程(iii)で室温まで冷却した丸鋼材に対して軟化処理することなく施す必要がある。なお、総真ひずみεは、下記の式を用いて求めた値である。
ε=ln(A0/Af)
ただし、「A0」および「Af」はそれぞれ、冷間伸線加工前の丸鋼材の断面積および最終冷間伸線加工後の鋼線の断面積を指す。 Step (iv): A step of performing cold drawing of 2.3 or more in total true strain to form a steel wire having a final wire diameter of 2.9 mm or more. The chemical composition described in the above section (A) is included. The round steel material which performed the process from the said process (i) to the process (iii) in order is cold-drawn. In particular, by setting the total true strain by cold drawing to 2.3 or more, the tensile strength can be as high as 2000 MPa or more, and the degree of orientation of the {110} crystal plane of the bcc phase is 0. .95 or more. For this reason, the total true strain by cold drawing is set to 2.3 or more. The preferable lower limit of the total true strain of the cold wire drawing is 2.5, and the preferable upper limit is 3.0. As long as the total true strain is 2.3 or more, the number of cold drawing processes is not particularly limited, and may be one or more. However, the cold wire drawing in step (iv) needs to be performed without softening the round steel material cooled to room temperature in step (iii). The total true strain ε is a value obtained using the following equation.
ε = ln (A 0 / A f )
However, “A 0 ” and “A f ” respectively indicate the cross-sectional area of the round steel material before cold drawing and the cross-sectional area of the steel wire after final cold drawing.
上記の冷間伸線加工の後、残留ひずみ除去のために鋼線に対して、200~450℃に10秒~30分加熱して時効処理を施してもよい。時効処理の加熱温度が200℃未満ではその効果が十分得られず、450℃を超えると引張強さが大幅に低下するためである。さらに、上記200~450℃の温度域での保持時間が10秒未満では、その効果が十分得られないし、30分を超えて保持してもその効果が飽和して製造コストの上昇を招くだけである。上記の時効処理温度は鋼線における表面の温度を指す。なお、時効処理での冷却は、大気中での放冷が好ましい。 Step (v): Step of heating at 200 to 450 ° C. for 10 seconds to 30 minutes After the above cold wire drawing, the steel wire is heated to 200 to 450 ° C. to remove residual strain. The aging treatment may be performed by heating for 2 to 30 minutes. This is because if the heating temperature of the aging treatment is less than 200 ° C., the effect cannot be obtained sufficiently, and if it exceeds 450 ° C., the tensile strength is greatly reduced. Furthermore, if the holding time in the temperature range of 200 to 450 ° C. is less than 10 seconds, the effect cannot be sufficiently obtained, and even if the holding time exceeds 30 minutes, the effect is saturated and only the production cost is increased. It is. The above aging temperature refers to the surface temperature of the steel wire. In addition, the cooling in the aging treatment is preferably carried out in the air.
最終線径の各鋼線について、長手方向に垂直な断面を鏡面研磨した後、ピクラール液でエッチングを行い、走査型顕微鏡にて断面の(1/4)D(但し、「D」は鋼線の直径を表す。)の位置において任意の8視野を5000倍で観察して写真を撮影し、目視にてパーライト部分を決定し、それを画像解析して金属組織におけるパーライトの面積率を求めた。 <1> Perlite area ratio:
For each steel wire of the final wire diameter, a cross section perpendicular to the longitudinal direction is mirror-polished and then etched with a Picral solution, and (1/4) D (where "D" is the steel wire) of the cross section with a scanning microscope In the position of 8), arbitrary 8 fields of view were observed at a magnification of 5000, a photograph was taken, a pearlite portion was visually determined, and image analysis was performed to determine the area ratio of pearlite in the metal structure. .
最終線径の各鋼線から、JIS Z 2241(2011)に準拠して9B号の引張試験片を採取して、室温の大気中で引張試験して、引張強さを求めた。 <2> Tensile properties:
From each steel wire having the final wire diameter, a tensile test piece of No. 9B was sampled in accordance with JIS Z 2241 (2011), and subjected to a tensile test in the air at room temperature to obtain a tensile strength.
上記〈2〉の調査で1700MPa以上の引張強さが得られた試験番号について、最終線径の各鋼線に深さ0.5mm、角度60°、切欠き底半径0.1mmの切欠きを設けた試験片を用いて、下記の方法で耐遅れ破壊特性を調査した。 <3> Delayed fracture resistance:
For the test numbers for which a tensile strength of 1700 MPa or more was obtained in the investigation of <2> above, a notch having a depth of 0.5 mm, an angle of 60 °, and a notch bottom radius of 0.1 mm was formed on each steel wire of the final wire diameter. Using the provided test specimen, the delayed fracture resistance was investigated by the following method.
上記〈2〉の調査で1700MPa以上の引張強さが得られた試験番号について、最終線径の各鋼線について、前記(B)項で述べた方法によって、金属組織におけるbcc相の{110}結晶面の配向度(F)を算出した。 <4> Degree of orientation of {110} crystal plane of bcc phase:
For the test numbers for which a tensile strength of 1700 MPa or more was obtained in the investigation of <2> above, each steel wire having the final wire diameter was {110} of the bcc phase in the metal structure by the method described in the above section (B). The degree of orientation (F) of the crystal plane was calculated.
Claims (3)
- 化学組成が、質量%で、
C:0.60~1.1%、
Si:0.05~1.5%、
Mn:0.30~1.5%、
P:0.030%以下、
S:0.030%以下、
Al:0.005~0.05%、
N:0.001~0.006%、
Cr:0~1.5%、
Ti:0~0.02%、
B:0~0.005%、
残部:Feおよび不純物からなり、
金属組織が、パーライトからなりかつ、長手方向に垂直な断面において、bcc相の{110}結晶面の配向度が0.95以上であり、
線径が、2.9mm以上である、
耐遅れ破壊特性に優れた鋼線。 Chemical composition is mass%,
C: 0.60 to 1.1%
Si: 0.05 to 1.5%,
Mn: 0.30 to 1.5%,
P: 0.030% or less,
S: 0.030% or less,
Al: 0.005 to 0.05%,
N: 0.001 to 0.006%,
Cr: 0 to 1.5%,
Ti: 0 to 0.02%,
B: 0 to 0.005%,
The balance: Fe and impurities,
The metal structure is made of pearlite, and in a cross section perpendicular to the longitudinal direction, the orientation degree of the {110} crystal plane of the bcc phase is 0.95 or more,
The wire diameter is 2.9 mm or more,
Steel wire with excellent delayed fracture resistance. - 前記化学組成が、質量%で、
Cr:0.10~1.5%を含有する、
請求項1に記載の耐遅れ破壊特性に優れた鋼線。 The chemical composition is mass%,
Containing Cr: 0.10 to 1.5%,
The steel wire excellent in delayed fracture resistance according to claim 1. - 前記化学組成が、質量%で、
Ti:0.003~0.02%、および、
B:0.0005~0.005%、
から選択される1種以上を含有する、
請求項1または2に記載の耐遅れ破壊特性に優れた鋼線。 The chemical composition is mass%,
Ti: 0.003-0.02%, and
B: 0.0005 to 0.005%,
Containing one or more selected from
A steel wire excellent in delayed fracture resistance according to claim 1 or 2.
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JP2003082437A (en) * | 2001-09-10 | 2003-03-19 | Kobe Steel Ltd | High strength steel wire having excellent strain age embrittlement resistance and longitudinal crack resistance, and production method therefor |
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JP2003082437A (en) * | 2001-09-10 | 2003-03-19 | Kobe Steel Ltd | High strength steel wire having excellent strain age embrittlement resistance and longitudinal crack resistance, and production method therefor |
WO2011055746A1 (en) * | 2009-11-05 | 2011-05-12 | 新日本製鐵株式会社 | High-carbon steel wire material with excellent processability |
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 |
JP2014055316A (en) * | 2012-09-11 | 2014-03-27 | Kobe Steel Ltd | Wire material for high strength steel wire |
JP2014177692A (en) * | 2013-03-15 | 2014-09-25 | Kobe Steel Ltd | Method of producing steel material excellent in cold workability and grindability |
JP2014208901A (en) * | 2013-03-28 | 2014-11-06 | 株式会社神戸製鋼所 | Wire rod for high strength steel wire excellent in cold drawability and hight strength steel wire |
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KR102139255B1 (en) | 2020-07-29 |
KR20180110002A (en) | 2018-10-08 |
CN109072376B (en) | 2020-10-23 |
CN109072376A (en) | 2018-12-21 |
JP6347311B2 (en) | 2018-06-27 |
JPWO2017170439A1 (en) | 2018-08-16 |
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