WO2023234702A1 - Fil-machine d'acier non trempé et non revenu pour le forgeage à chaud présentant une excellente usinabilité et une excellente ténacité aux chocs et son procédé de fabrication - Google Patents

Fil-machine d'acier non trempé et non revenu pour le forgeage à chaud présentant une excellente usinabilité et une excellente ténacité aux chocs et son procédé de fabrication Download PDF

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Publication number
WO2023234702A1
WO2023234702A1 PCT/KR2023/007444 KR2023007444W WO2023234702A1 WO 2023234702 A1 WO2023234702 A1 WO 2023234702A1 KR 2023007444 W KR2023007444 W KR 2023007444W WO 2023234702 A1 WO2023234702 A1 WO 2023234702A1
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WIPO (PCT)
Prior art keywords
impact toughness
wire rod
mns
improved machinability
clause
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PCT/KR2023/007444
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English (en)
Korean (ko)
Inventor
임남석
문동준
김한휘
Original Assignee
주식회사 포스코
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Publication of WO2023234702A1 publication Critical patent/WO2023234702A1/fr

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Classifications

    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the present invention relates to a non-quenched wire with improved machinability and impact toughness and a manufacturing method thereof. More specifically, it relates to a non-quenched wire suitable for use as a material for automobiles or machine parts and a manufacturing method thereof.
  • non-quenched steel omits the QT heat treatment process. Therefore, non-quenched steel not only has economic advantages such as reduced heat treatment costs, shortened delivery time due to simplification of the process, and improved productivity, but is also an environmentally friendly steel that can be expected to reduce CO 2 generated by operating the furnace during heat treatment.
  • non-quenched steel had relatively inferior toughness compared to tempered steel, so it was applied only to parts that did not require significant toughness.
  • machinability is also required. To improve machinability, a large amount of MnS is generally created by adding S, which causes the problem of deterioration of product toughness.
  • One aspect of the present invention is to overcome the inferior toughness compared to existing tempered steel and to provide a non-quenched wire rod and a manufacturing method thereof that can simultaneously secure machinability and impact toughness without additional heat treatment through the addition of high S and high N. .
  • the non-tempered wire material with improved machinability and impact toughness has a weight percentage of C: 0.3-0.5%, Si: 0.4-0.9%, Mn: 0.5-1.2%, P: 0.02% or less, S : 0.01 ⁇ 0.05%, sol.Al: 0.01 ⁇ 0.05%, Cr 0.1% ⁇ 0.3%, Ti: 0.01% ⁇ 0.02%, Ca: 0.0005% ⁇ 0.002%, N: 0.007% ⁇ 0.02%, remaining Fe and inevitable It contains impurities, contains ferrite and pearlite as a microstructure, satisfies the following relational equation 1, and has an area fraction of MnS in the range of 0.10 to 0.60%.
  • a non-tempered wire with improved machinability and impact toughness may have a number density of MnS of 70 pieces/mm 2 or more and an aspect ratio of MnS of 40 or less.
  • a non-tempered wire material with improved machinability and impact toughness may have a tensile strength of 700 MPa or more, a yield strength of 350 to 500 MPa, and a yield ratio of 0.45 to 0.65.
  • a non-tempered wire material with improved machinability and impact toughness may have an impact toughness of 60 J/cm 2 or more, and the product of tensile strength and impact toughness may be 45,000 MPa ⁇ J/cm 2 or more.
  • the method of manufacturing a non-tempered wire with improved machinability and impact toughness according to an embodiment of the present invention is calculated by weight percentage, C: 0.3 to 0.5%, Si: 0.4 to 0.9%, Mn: 0.5 to 1.2%, P: 0.02%.
  • the wire has ferrite and pearlite as a microstructure. It contains, satisfies the above relational expression 1, and the area fraction of MnS is 0.10 to 0.60%.
  • Ti and Al combine with N to form nitrides of TiN and AlN, and these nitrides interfere with grain boundary growth to refine the grain size and improve toughness.
  • Ca-based oxides resulting from the addition of Ca act as MnS formation nuclei, suppressing MnS elongation during rolling and improving machinability and toughness. Therefore, even if heat treatment is omitted, it can be applied to automotive materials or mechanical parts materials that require both machinability and toughness.
  • the non-tempered wire material with improved machinability and impact toughness has a weight percentage of C: 0.3-0.5%, Si: 0.4-0.9%, Mn: 0.5-1.2%, P: 0.02% or less, S : 0.01 ⁇ 0.05%, sol.Al: 0.01 ⁇ 0.05%, Cr 0.1% ⁇ 0.3%, Ti: 0.01% ⁇ 0.02%, Ca: 0.0005% ⁇ 0.002%, N: 0.007% ⁇ 0.02%, remaining Fe and inevitable It contains impurities, contains ferrite and pearlite as a microstructure, satisfies the following relational equation 1, and has an area fraction of MnS in the range of 0.10 to 0.60%.
  • the present inventors examined various angles to provide a wire that can secure machinability and impact toughness, and as a result, it was found that machinability and toughness can be secured without separate heat treatment by appropriately controlling the alloy composition and microstructure of the wire. discovered and completed the present invention.
  • the non-tempered wire material with improved machinability and impact toughness contains, in weight percent, C: 0.3 to 0.5%, Si: 0.4 to 0.9%, Mn: 0.5 to 1.2%, P: 0.02% or less, S : 0.01 ⁇ 0.05%, sol.Al: 0.01 ⁇ 0.05%, Cr 0.1% ⁇ 0.3%, Ti: 0.01% ⁇ 0.02%, Ca: 0.0005% ⁇ 0.002%, N: 0.007% ⁇ 0.02%, the rest Fe and inevitable It contains impurities, contains ferrite and pearlite as a microstructure, satisfies the following relational equation 1, and has an area fraction of MnS of 0.10 to 0.60%.
  • the C content is 0.3 to 0.5%.
  • C is an element that plays a role in improving the strength of wire rods. In order to achieve the above-mentioned effects, it is preferable to contain 0.3% or more of C. However, if the content is excessive, toughness and machinability may deteriorate, so it is desirable to limit the upper limit of the C content to 0.5%.
  • the Si content is 0.4 to 0.9%.
  • Si is a useful element as a deoxidizer and an element that plays a role in improving strength. If the Si content is less than 0.4%, the above-described effect cannot be achieved, and if it exceeds 0.9%, the deformation resistance of the steel rapidly increases due to solid solution strengthening, which may deteriorate cold workability. Therefore, in the present invention, the upper limit of the Si content is limited to 0.9%.
  • the content of Mn is 0.5 to 1.2%.
  • Mn is a useful element as a deoxidizing agent and desulfurizing agent. If the Mn content is less than 0.5%, the above-described effect cannot be achieved, and if the Mn content exceeds 1.2%, the strength of the steel itself becomes too high, the deformation resistance of the steel rapidly increases, and cold workability may deteriorate. Accordingly, the upper limit of the Mn content is limited to 1.2%.
  • the Cr content is 0.1 to 0.3% or less.
  • Cr is an element that promotes ferrite and pearlite transformation during hot rolling. In addition, without increasing the strength of the steel itself more than necessary, it reduces the amount of dissolved carbon by precipitating carbides in the steel and contributes to the reduction of dynamic strain aging caused by dissolved carbon. If the Cr content is less than 0.1%, the above-described effect cannot be achieved, and if it exceeds 0.3%, the strength of the steel itself becomes excessively high and the deformation resistance of the steel rapidly increases, which may result in deterioration of cold workability. Accordingly, the upper limit of Cr content is limited to 0.3%.
  • the P content is 0.02% or less.
  • P is an unavoidably contained impurity and is an element that segregates at grain boundaries, lowering the toughness of steel, and is the main cause of reduced delayed fracture resistance. Therefore, in the present invention, it is desirable to control the content as low as possible. In theory, it is advantageous to control the P content at 0%, but since it is inevitably contained during the manufacturing process, it is important to manage the upper limit, and in the present invention, the upper limit of the P content is managed at 0.02%.
  • the S content is 0.01 to 0.05%.
  • S is an element that segregates at grain boundaries, greatly reducing the ductility of steel, and forms emulsions in steel, deteriorating delayed fracture resistance and stress relaxation characteristics. It is an impurity that is inevitably contained during the manufacturing process. However, as in the present invention, S is actively used to improve cutting performance. S improves machinability by combining with Mn to form MnS. In the present invention, the content of S, which is effective in improving machinability without significantly reducing the toughness of the steel, is considered and is managed in the range of 0.01% to 0.05%.
  • the content of Sol.Al is 0.01 ⁇ 0.05%.
  • sol.Al is an element that acts usefully as a deoxidizing agent.
  • sol.Al may be included in an amount of 0.01% or more.
  • the upper limit of Al content is limited to 0.05%.
  • the content of Ti is 0.01 to 0.02%.
  • Titanium (Ti) is an element that plays a major role in improving the toughness of steel by forming TiN precipitates during the solidification process of steel, suppressing austenite grain growth during the heating and hot rolling process of slabs, and refining the grain size of the final structure. If the Ti content is less than 0.01%, TiN precipitates are insufficient and it is difficult to secure a sufficient amount to limit the movement of austenite grain boundaries. On the other hand, if it exceeds 0.02%, there is a problem that coarse titanium nitride is generated and the toughness is deteriorated, so in the present invention, the upper limit of the Ti content is limited to 0.02%.
  • the Ca content is 0.0005 ⁇ 0.002%.
  • Ca is an essential element to realize the effect of improving machinability and impact toughness by reducing the MnS aspect ratio.
  • oxide acts as a nucleus for MnS generation and suppresses the elongation of MnS during wire rod rolling, thereby maintaining a low aspect ratio.
  • the low aspect ratio of MnS not only improves machinability but also alleviates microstructure anisotropy to prevent deterioration of toughness.
  • Ca in order to achieve the above-mentioned effect, Ca must be included in an amount of 0.0005% or more, but if the Ca content exceeds 0.002%, there may be difficulties in manufacturing. Therefore, in the present invention, the upper limit of Ca content is limited to 0.002%.
  • the N content is 0.007 to 0.02%.
  • N is an essential element for improving impact toughness by forming nitrides with Ti and Al to refine the particle size. If the N content is less than 0.007%, it is difficult to secure sufficient nitride and the amount of precipitates such as Al and Ti is reduced, making it impossible to secure the toughness targeted by the present invention. If the N content exceeds 0.02%, nitride is used. As non-existent dissolved nitrogen increases, the toughness and ductility of the wire rod may decrease. Therefore, in the present invention, the upper limit of the N content is limited to 0.02%.
  • the non-roughened wire rod of the present invention may contain other impurities that may be included during the industrial production process of ordinary steel. Since these impurities are known to anyone with ordinary knowledge in the technical field to which the present invention pertains, the type and content thereof are not particularly limited in the present invention.
  • the non-quenched wire rod according to an embodiment of the present invention may satisfy the following relational equation 1.
  • Equation 1 [S] and [Mn] each mean the content (% by weight) of the corresponding element.
  • Equation 1 is a formula related to machinability.
  • MnS is formed by adding high S and Mn.
  • MnS is an elongated inclusion that has an elongated shape and direction in the rolling direction and greatly improves the machinability of the medium-carbon, non-tempered wire rod according to the present invention.
  • MnS acts as a crack initiation point and propagation path upon impact, thereby deteriorating impact toughness. If the ratio of [Mn]/[S] is less than 20, machinability may be satisfactory, but impact toughness may decrease, and if it exceeds 70, machinability may not be sufficient. Therefore, in the present invention, the ratio of [Mn]/[S] is limited to 20 to 70, and preferably 30 to 60.
  • the non-tempered steel according to an embodiment of the present invention may have an area fraction of MnS of 0.10 to 0.60%, preferably 0.15 to 0.50%, and more preferably 0.15 to 0.45%.
  • the non-tempered steel according to an embodiment of the present invention may include a number density of MnS of 70 pieces/mm 2 or more, preferably 80 pieces/mm 2 or more, and more preferably It may contain more than 90 pieces/mm 2 .
  • MnS As the density of MnS increases, it acts as a stress concentration source during cutting, reducing cutting resistance and improving cutting performance. To achieve this, the density of MnS must be at least 70 pieces/mm 2 or more.
  • the non-tempered steel according to an embodiment of the present invention may have an aspect ratio of MnS of 40 or less, preferably 30 or less, and more preferably 20 or less. At this time, if the aspect ratio of MnS exceeds 40, impact toughness can rapidly decrease.
  • non-quenched steel according to an embodiment of the present invention may have a tensile strength of 700 MPa or more.
  • non-tempered steel according to an embodiment of the present invention may have a yield strength of 350 to 500 MPa.
  • non-quenched steel according to an embodiment of the present invention may have a yield ratio of 0.45 to 0.65.
  • non-quenched steel according to an embodiment of the present invention may have an impact toughness of 60 J/cm 2 or more.
  • the product of tensile strength and impact toughness of the non-quenched steel according to an embodiment of the present invention may be 45,000 MPa ⁇ J/cm 2 or more.
  • the non-tempered wire material with improved machinability and impact toughness contains, in weight percent, C: 0.3 to 0.5%, Si: 0.4 to 0.9%, Mn: 0.5 to 1.2%, P: 0.02% or less, S : 0.01 ⁇ 0.05%, sol.Al: 0.01 ⁇ 0.05%, Cr 0.1% ⁇ 0.3%, Ti: 0.01% ⁇ 0.02%, Ca: 0.0005% ⁇ 0.002%, N: 0.007% ⁇ 0.02%, the rest Fe and inevitable Reheating a steel piece containing impurities and containing ferrite and pearlite as a microstructure at a temperature range of 950 to 1120°C; Manufacturing a wire rod by finishing rolling the reheated steel piece at 750 to 850°C; and a step of cooling the wire after winding it, wherein the cooling step after winding includes cooling the wire to 400°C at an average cooling rate of 0.1 to 5.0°C/s, and the wire has ferrite and pearlite as
  • the reheating step is a step of reheating the rolled billet and is a step to lower the rolling load during wire rod rolling. At this time, reheating may be performed at a temperature of 950 to 1120°C. If the reheating temperature of the steel piece is less than 950°C, the rolling load may increase, which may cause manufacturing difficulties. On the other hand, if it exceeds 1,120°C, the AlN finely generated in the steel piece will be re-dissolved during heating, significantly reducing the effect of grain size refinement. .
  • the reheated steel pieces are hot rolled to manufacture wire rods.
  • the final rolling temperature of hot rolling may be 750 to 850°C. If the finish rolling temperature is less than 750°C, the rolling load may increase, and if it exceeds 850°C, the grains may become coarse, making it difficult to secure the high toughness targeted by the present invention.
  • a process of winding the wire manufactured according to the above into a coil shape may be performed, and at this time, the winding temperature may be 750 to 850°C. Since the temperature of the wire obtained by the finish rolling may increase due to transformation heat generation, the temperature of the wire immediately before winding may be higher than the temperature at which the finish rolling is performed. At this time, depending on the temperature raised by the heat generation, coiling can be performed after cooling to the above coiling temperature, or coiling can be performed without additional cooling. If the coiling temperature is less than 750°C, the surface layer martensite generated during cooling cannot be recovered by reheating, and tempered martensite is generated, which increases the possibility of causing surface defects during wire drawing. On the other hand, if the temperature exceeds 850°C, thick scale is formed on the surface of the wire, which not only makes it easy to cause surface defects during descaling, but also increases the cooling time during subsequent cooling, which may reduce productivity.
  • the wound wire can be subjected to a cooling process, and at this time, the cooling rate is characterized by cooling to 400°C at an average cooling rate in the range of 0.1 to 5.0°C/s through air cooling or controlled cooling after hot forging. If the average cooling rate up to 400°C after winding is less than 0.1°C/s, the target strength cannot be satisfied due to excessive production of proeutectoid ferrite, and if it exceeds 5°C/s, low-temperature structures such as martensite are generated. Toughness and machinability may be reduced.
  • Bloom having the alloy composition shown in Table 1 below was heated at 1,200°C for 4 hours and then rolled into steel pieces at a finish rolling temperature of 1,100°C to obtain a billet. Thereafter, the billet was heated for 90 minutes under the temperature conditions shown in Table 2 below, then finish rolled at 800°C, coiled at 780°C, and then cooled under the temperature conditions shown in Table 2 below to produce a wire rod with a diameter of 26 mm.
  • Wire rods having the composition of invention steels 1 to 7 and comparative steels 1 to 6 were manufactured (Table 1), and the machinability, tensile strength, and impact toughness of the collected wire specimens were measured.
  • the room temperature tensile strength was measured by collecting from the center of the untreated steel specimen at 25°C, and the room temperature impact toughness was obtained by performing a Charpy impact test on a specimen with a U-notch (based on U-notch standard sample, 10x10x55mm) at 25°C. It was evaluated based on the impact energy value.
  • a wire rod with a diameter of 26 mm was manufactured into a CD-Bar (Cold Drawn Bar) with a diameter of 24 mm by applying a reduction ratio of 14.8%. Machinability was evaluated using a CNC lathe, and a CD-Bar with a diameter of 24 mm was turned until its diameter was 15 mm, and then the degree of wear of the turning tool was evaluated. At this time, cutting conditions were performed using cutting oil under the conditions of a cutting speed of 100 mm/min, a feed rate of 0.1 mm/rev, and a cutting depth of 1.0 mm, and the cutting tool used was a cermet material tool with a chip breaker. . The wear depth of the tool was measured by measuring the depth of the flank wear surface after continuously machining 300 parts with the above-mentioned shape, and anything exceeding 0.2mm was judged to be defective, and anything less than 0.2mm was judged to be good.
  • the area fraction of MnS, the number density of MnS, and the aspect ratio of MnS were analyzed using image analysis software by taking 20 pictures of each L cross-section of the wire with an optical microscope at a magnification of 200 times.
  • Comparative Example 1 had poor tool wear due to high strength outside the range of carbon content, and Comparative Examples 2 and 3 had insufficient impact toughness due to excessive Si and Mn contents.
  • Comparative Example 4 had poor impact toughness because the Ti content was insufficient and the particle size refinement effect was not sufficiently achieved.
  • Comparative Example 5 impact toughness was reduced due to the large aspect ratio of MnS, and in Comparative Example 6, the value of Equation (1) was not satisfied, and the fraction and density of MnS were insufficient, resulting in poor cutting tool wear.
  • Comparative Examples 7 to 9 although all chemical components were satisfied, had poor toughness or did not meet the target strength because the heating temperature and cooling rate were out of range.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention concerne un fil-machine d'acier non trempé et non revenu présentant des propriétés améliorées d'usinabilité et de ténacité et son procédé de fabrication, le fil-machine non trempé et non revenu, selon la présente invention, comprenant, en pourcentage en poids : C : de 0,3 à 0,5 % ; Si : de 0,4 à 0,9 % ; Mn : de 0,5 à 1,2 % ; P : au plus 0,02 % ; S : de 0,01 à 0,05 % ; Al sol. : de 0,01 à 0,05 % ; Cr : de 0,1 à 0,3 % ; Ti : de 0,01 à 0,02 % ; Ca : de 0,0005 à 0,002 % ; N : de 0,007 à 0,02 % ; et le complément étant constitué de Fe et d'impuretés inévitables, et comprenant de la ferrite et de la perlite en tant que microstructure, l'expression relationnelle 1 suivante étant satisfaite, et la fraction surfacique de MnS satisfaisant à de 0,10 à 0,60 %. [Expression relationnelle 1] 20 ≤ [Mn]/[S] ≤ 70
PCT/KR2023/007444 2022-05-31 2023-05-31 Fil-machine d'acier non trempé et non revenu pour le forgeage à chaud présentant une excellente usinabilité et une excellente ténacité aux chocs et son procédé de fabrication WO2023234702A1 (fr)

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KR10-2022-0066880 2022-05-31
KR20220066880 2022-05-31

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WO2023234702A1 true WO2023234702A1 (fr) 2023-12-07

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002226939A (ja) * 2001-02-01 2002-08-14 Daido Steel Co Ltd 軟窒化用非調質鋼
JP2008231544A (ja) * 2007-03-23 2008-10-02 Sumitomo Metal Ind Ltd 非調質鋼材およびその製造方法
US20100183473A1 (en) * 2007-10-29 2010-07-22 Shinya Teramoto Martensite type hot forging use non heat-treated steel and hot forged non heat-treated steel part
KR20120049405A (ko) * 2008-02-26 2012-05-16 신닛뽄세이테쯔 카부시키카이샤 파단 분리성 및 피삭성이 우수한 열간 단조용 비조질강과 열간 압연 강재 및 열간 단조 비조질강 부품
KR101630978B1 (ko) * 2014-12-11 2016-06-16 주식회사 포스코 냉간가공성이 우수한 비조질 선재 및 그 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002226939A (ja) * 2001-02-01 2002-08-14 Daido Steel Co Ltd 軟窒化用非調質鋼
JP2008231544A (ja) * 2007-03-23 2008-10-02 Sumitomo Metal Ind Ltd 非調質鋼材およびその製造方法
US20100183473A1 (en) * 2007-10-29 2010-07-22 Shinya Teramoto Martensite type hot forging use non heat-treated steel and hot forged non heat-treated steel part
KR20120049405A (ko) * 2008-02-26 2012-05-16 신닛뽄세이테쯔 카부시키카이샤 파단 분리성 및 피삭성이 우수한 열간 단조용 비조질강과 열간 압연 강재 및 열간 단조 비조질강 부품
KR101630978B1 (ko) * 2014-12-11 2016-06-16 주식회사 포스코 냉간가공성이 우수한 비조질 선재 및 그 제조방법

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