KR100478091B1 - Method for Manufacturing Galvanized Steel Sheet - Google Patents
Method for Manufacturing Galvanized Steel Sheet Download PDFInfo
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- KR100478091B1 KR100478091B1 KR10-2002-0028874A KR20020028874A KR100478091B1 KR 100478091 B1 KR100478091 B1 KR 100478091B1 KR 20020028874 A KR20020028874 A KR 20020028874A KR 100478091 B1 KR100478091 B1 KR 100478091B1
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- galvanized steel
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 22
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 19
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 19
- 238000000034 method Methods 0.000 title claims abstract description 11
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 81
- 239000010959 steel Substances 0.000 claims abstract description 81
- 238000007747 plating Methods 0.000 claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 11
- 238000005246 galvanizing Methods 0.000 claims abstract description 8
- 238000005098 hot rolling Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 239000011701 zinc Substances 0.000 claims description 9
- 229910052745 lead Inorganic materials 0.000 claims description 6
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 238000010276 construction Methods 0.000 abstract description 3
- 230000002787 reinforcement Effects 0.000 abstract description 3
- 239000000463 material Substances 0.000 description 23
- 238000010438 heat treatment Methods 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 9
- 230000007547 defect Effects 0.000 description 9
- 229910000746 Structural steel Inorganic materials 0.000 description 6
- 238000005097 cold rolling Methods 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 238000005554 pickling Methods 0.000 description 4
- 238000004804 winding Methods 0.000 description 4
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 3
- 238000012937 correction Methods 0.000 description 3
- 238000005238 degreasing Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 230000007257 malfunction Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000013077 target material Substances 0.000 description 2
- 239000004254 Ammonium phosphate Substances 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910000148 ammonium phosphate Inorganic materials 0.000 description 1
- 235000019289 ammonium phosphates Nutrition 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- MNNHAPBLZZVQHP-UHFFFAOYSA-N diammonium hydrogen phosphate Chemical compound [NH4+].[NH4+].OP([O-])([O-])=O MNNHAPBLZZVQHP-UHFFFAOYSA-N 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
- B21B1/22—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 plates, strips, bands or sheets of indefinite length
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/16—Control of thickness, width, diameter or other transverse dimensions
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C22/00—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C22/70—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using melts
- C23C22/72—Treatment of iron or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
-
- 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
- B21B1/22—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 plates, strips, bands or sheets of indefinite length
- B21B2001/228—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 plates, strips, bands or sheets of indefinite length skin pass rolling or temper rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/02—Transverse dimensions
- B21B2261/04—Thickness, gauge
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/20—Temperature
Abstract
본 발명은 고강도가 요구되는 데크플레이트(Deck Plate), 스틸하우스 스터드 (Stud), 천정 보강재, 건설현장에서 사용하는 족장판(足場板) 등에 사용되는 고항복비형 고강도 용융아연도금강판을 제조하는 방법에 관한 것으로서, 작업성이 우수할 뿐만 아니라 높은 항복강도, 높은 인장강도 및 적정 연성의 기계적인 특성은 물론 우수한 표면특성, 형상 및 도금밀착성을 확보할 수 있는 냉연용융아연도금강판의 제조방법을 제공하고자 하는데, 그 목적이 있는 것이다,The present invention is a method for producing a high yield ratio type high strength hot-dip galvanized steel sheet used in deck plates, steel house studs, ceiling reinforcement, chief plate used in construction sites that require high strength The present invention relates to a method for manufacturing a cold-rolled hot-dip galvanized steel sheet which not only has excellent workability but also has high yield strength, high tensile strength and mechanical properties of appropriate ductility, as well as excellent surface properties, shape and plating adhesion. I want to do that, but there is a purpose,
본 발명은 용융아연도금강판을 제조하는 방법에 있어서,The present invention provides a method for producing a hot-dip galvanized steel sheet,
중량%로, C: 50ppm이하, Si : 0.03%이하, Mn : 0.8∼1.0%, P : 0.08~1.0%, S : 0.015%이하, Al : 0.02∼0.06%, Ti: 0.04~0.06%, B: 5~15ppm, 잔부 Fe 및 기타 불가피한 불순물로 이루어진 강 슬라브를 가열로에서 1150∼1250℃로 가열한 후, 880~940℃의 열간압연 마무리 온도조건으로 열간압연하고, 580∼650℃에서 권취한 다음, 열연강판을 산세한 후, 냉간압연한 다음, 탈지후, 650~700℃로 가열한 다음, 440~465℃로 냉각한 후, 용융아연도금욕에서 도금한 다음, 0.7%이하의 연신율로 조질압연하여 용융아연도금강판을 제조하는 방법에 관한 것이다. By weight%, C: 50 ppm or less, Si: 0.03% or less, Mn: 0.8-1.0%, P: 0.08-1.0%, S: 0.015% or less, Al: 0.02-0.06%, Ti: 0.04-0.06%, B : Steel slab consisting of 5 ~ 15ppm, balance Fe and other unavoidable impurities is heated in the furnace to 1150 ~ 1250 ℃, hot rolled at 880 ~ 940 ℃ hot rolling finish temperature condition and wound up at 580 ~ 650 ℃. Next, the hot rolled steel sheet was pickled, cold rolled, degreased, heated to 650 to 700 ° C., cooled to 440 to 465 ° C., plated in a hot dip galvanizing bath, and elongated at an elongation of 0.7% or less. The present invention relates to a method of manufacturing hot-dip galvanized steel sheet by rough rolling.
Description
본 발명은 고강도가 요구되는 데크플레이트(Deck Plate), 스틸하우스 스터드 (Stud), 천정 보강재, 건설현장에서 사용하는 족장판(足場板) 등에 사용되는 고항복비형 고강도 용융아연도금강판(Cold Rolled Galvanized Iron : 이하, "CGI"이라고도 칭함)을 제조하는 방법에 관한 것으로서, 보다 상세하게는 고항복비형 인장강도 570MPa이상의 고강도 용융아연도금강판을 제조하는 방법에 관한 것이다.The present invention is a high yield ratio high strength hot-dip galvanized steel sheet used in deck plates, steel house studs, ceiling reinforcement, chief plate used in construction sites requiring high strength Iron (hereinafter also referred to as "CGI"), and more particularly, to a method of producing a high strength hot dip galvanized steel sheet having a high yield ratio tensile strength of 570 MPa or more.
CGI는 고항복비형 고강도 용융아연도금강판으로서, 고강도가 요구되는 데크플레이트(Deck Plate), 스틸하우스 스터드 (Stud), 천정 보강재, 건설현장에서 사용하는 족장판(足場板) 등에 사용되고 있다.CGI is a high yield ratio high strength hot-dip galvanized steel sheet, and is used in deck plates, steel house studs, ceiling reinforcements, and chief plates used in construction sites.
최근, 국내외 고객사들이 경제 불황기를 맞아 지속적인 원가절감을 위해 기존 CGI 일반강, 400MPa이하의 구조용강의 강판두께를 낮추고 강도가 높아진 인장강도 570MPa이상의 고강도강판 공급요구와 스틸하우스(Steel House) 보급이 늘어나면서 강재소요가 지속증가 되어 왔다. Recently, domestic and overseas customers have faced economic downturns, so as to reduce costs, lower the steel sheet thickness of existing CGI general steels and structural steels below 400 MPa, and increase the demand for high-strength steel plates with a higher tensile strength of more than 570 MPa and the expansion of Steel House. Steel demand has been increasing.
특히, 인장강도 570MPa이상의 고강도에 항복강도가 560MPa이상인 고항복비형으로 적정 연신율을 보유하는 CGI강판 개발 필요성이 대두되고 있다. In particular, there is a need to develop a CGI steel sheet having an appropriate elongation at high yield ratio type having a high strength of 570 MPa or more and a yield strength of 560 MPa or more.
이러한 기계적성질을 보유하는 강판은 굽힘가공이 용이하고 가공후 외부하중이나 충격,화재 등에 대한 변형저항이 뛰어나 강판두께를 하향 시킬 수 있게 된다.The steel sheet having such mechanical properties is easy to bend and be excellent in deformation resistance to external loads, impacts, fires, etc., after processing, so that the steel sheet thickness can be lowered.
인장강도 570MPa급 CGI 구조용강을 제조하는 종래의 방법으로는 중저, 저탄소강에 Ti첨가, 중탄소강 또는 극저탄소강을 기본성분계로 하여 Ti를 첨가하여 출강 및 열간압연후 용융아연도금공정(Continuous Galvanizing Line: 이하 "CGL"이라고도 칭함)에서 재결정온도 이하 온도범위에서 열처리후 고속 라인 스피드(Line Speed)로 용융아연도금을 실시하는 방법이 알려져 있다.Conventional methods for producing tensile strength 570 MPa grade CGI structural steels include the addition of Ti to low, medium and low carbon steels, and the addition of Ti as a basic component system. Line (hereinafter also referred to as "CGL") is a method of hot-dip galvanizing at a high line speed after heat treatment in a temperature range below the recrystallization temperature.
상기와 같이 중저, 저탄소강에 Ti첨가, 중탄소강 또는 극저탄소강을 기본성분계로 하여 인장강도 570MPa이상의 고강도 구조용강을 제조할 경우에는 CGL열처리 온도 및 라인 스피드에 민감하고, 재질불량 및 편차가 크고, 열처리온도가 중저탄소 Ti첨가강은 540~600℃, 극저Ti 첨가강은 580~620℃로 낮아 타 강종과의 연결작업이 곤란하여 재질불량 방지를 위해 항상 더미 코일(Dummy Coil)이 필요하고, 저온열처리로 인하여 CGL 로(Furnace)분위기가 불안정하고 또한 형상교정 능력이 열위하는 등 제품불량율이 20~30%이상 발생하는 문제점이 있다. As described above, when manufacturing high strength structural steel with a tensile strength of 570 MPa or more based on Ti addition, medium carbon steel or ultra low carbon steel as a basic component system, it is sensitive to CGL heat treatment temperature and line speed, and has large material defects and deviations. Since the heat treatment temperature is 540 ~ 600 ℃ for low and low carbon Ti additive steel and 580 ~ 620 ℃ for ultra low Ti added steel, it is difficult to connect with other steel grades, so a dummy coil is always needed to prevent material defects. In addition, CGL furnace atmosphere is unstable due to low temperature heat treatment and shape defection ability is inferior, resulting in a defective product rate of 20-30% or more.
또한, 상기 방법에서는 더미 코일이 정상판매가 곤란한 불량품으로 처리하여야 하며, 이 더미 코일을 생략하고 일반재 및 400MPa구조용강을 작업하다가 갑자기 온도하향시 로내 스트립(Strip)과 롤(Roll)온도차이가 크게 되어 스트립이 사행함으로써 결국 판파단이라는 사고를 유발하여 12시간이상의 공장 가동중단이라는 막대한 피해를 초래하게 되는 문제점이 있다. In addition, in the above method, the dummy coil should be treated as a defective product that is difficult to sell normally, and the difference between the strip and roll temperature is large when the temperature is suddenly lowered while omitting the dummy coil and working with the general material and the 400MPa structural steel. As the strip meanders, there is a problem that eventually causes an accident called pan breaking, causing enormous damage such as factory shutdown for more than 12 hours.
또한, 상기 방법에 의하면, 열연강판을 산세후 냉간압연한 풀 하드 코일(Full Hard Coil)은 1,000톤 이상의 롤 포스(Roll Force) 등으로 인해 강판의 에지(Edge)부 및중앙(Center)부 각각 또는 두 부분 모두에 웨이브(Wave)형태의 형상결함이 존재하는데, CGL 저온열처리로 인해 형상교정이 미흡하여 웨이브 결함으로 불량이 자주 발생하고, 평균 형상품질등급도 680℃이상의 타강종에 대비하여 절대적으로 열위하고, 그리고 이 형상품질 확보를 위해 생산속도를 하향하거나 열처리온도를 상향시키는 경우에는 강도가 떨어지는 문제점이 발생하게 된다.In addition, according to the method, the full hard coil (cold rolled) after pickling the hot rolled steel sheet, each of the edge portion and the center portion of the steel sheet due to the roll force of 1,000 tons or more Or, there are wave shape defects on both parts, and CGL low-temperature heat treatment results in insufficient shape correction, so that defects frequently occur due to wave defects, and the average shape quality grade is also absolute compared to other steel grades of 680 ℃ or higher. Inferior to, and when the production rate is lowered or the heat treatment temperature is increased to secure the shape quality, the strength is reduced.
본 발명자들은 상기한 종래 기술의 제반 문제점을 해결하기 위하여 연구 및 실험을 행하고, 그 결과에 근거하여 본 발명을 제안하게 된 것으로서, 본 발명은 작업성이 우수할 뿐만 아니라 높은 항복강도, 높은 인장강도 및 적정 연성의 기계적인 특성은 물론 우수한 표면특성, 형상 및 도금밀착성을 확보할 수 있는 냉연용융아연도금강판의 제조방법을 제공하고자 하는데, 그 목적이 있는 것이다,The present inventors have conducted research and experiment to solve the above-mentioned problems of the prior art, and proposed the present invention based on the results, and the present invention not only has excellent workability but also high yield strength and high tensile strength. And to provide a method of manufacturing a cold-rolled hot-dip galvanized steel sheet that can ensure a good ductility of the mechanical properties as well as excellent surface properties, shape and plating adhesion, the purpose is,
이하, 본 발명에 대하여 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated.
본 발명은 용융아연도금강판을 제조하는 방법에 있어서,The present invention provides a method for producing a hot-dip galvanized steel sheet,
중량%로, C: 50ppm이하, Si : 0.03%이하, Mn : 0.8∼1.0%, P : 0.08~1.0%, S : 0.015%이하, Al : 0.02∼0.06%, Ti: 0.04~0.06%, B: 5~15ppm, 잔부 Fe 및 기타 불가피한 불순물로 이루어진 강 슬라브를 가열로에서 1150∼1250℃로 가열한 후, 880~940℃의 열간압연 마무리 온도조건으로 열간압연하고, 580∼650℃에서 권취한 다음, 열연강판을 산세한 후, 냉간압연한 다음, 탈지후, 650~700℃로 가열한 다음, 440~465℃로 냉각한 후, 용융아연도금욕에서 도금한 다음, 0.7%이하의 연신율로 조질압연하여 용융아연도금강판을 제조하는 방법에 관한 것이다. By weight%, C: 50 ppm or less, Si: 0.03% or less, Mn: 0.8-1.0%, P: 0.08-1.0%, S: 0.015% or less, Al: 0.02-0.06%, Ti: 0.04-0.06%, B : Steel slab consisting of 5 ~ 15ppm, balance Fe and other unavoidable impurities is heated in the furnace to 1150 ~ 1250 ℃, hot rolled at 880 ~ 940 ℃ hot rolling finish temperature condition and wound up at 580 ~ 650 ℃. Next, the hot rolled steel sheet was pickled, cold rolled, degreased, heated to 650 to 700 ° C., cooled to 440 to 465 ° C., plated in a hot dip galvanizing bath, and elongated at an elongation of 0.7% or less. The present invention relates to a method of manufacturing hot-dip galvanized steel sheet by rough rolling.
이하, 본 발명에 대하여 상세히 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail.
먼저, 본 발명강의 조성에 대하여 설명한다.First, the composition of the inventive steel will be described.
상기 C은 강도확보 측면에서 가장 유효한 원소이나 중탄소강은 열연코일(강판)을 냉간압연할 시 압연부하가 발생하는 문제점이 있고, 중저 및 저탄소강은 CGL열처리온도가 600℃이하이어야 하므로 재질불량 및 편차가 크고 타강종과 연결작업 및 형상품질이 열위하는 문제점이 있다. The C is the most effective element in terms of securing strength, but there is a problem in that the rolling load occurs when cold rolling a hot rolled coil (steel sheet), and the low and medium carbon steel has a CGL heat treatment temperature of 600 ° C. or lower, so that the material is poor. There is a problem that the deviation is large and inferior to other steel grades and the work quality and shape.
따라서 본 발명에서는 CGL열처리시 재결정온도를 상향하여 650℃이상 열처리하여 재질 및 형상,작업성이 양호하게 되도록 C의 함량을 50ppm이하로 제한한 것이다.Therefore, in the present invention, the C content is limited to 50 ppm or less in order to improve the material, shape, and workability by increasing the recrystallization temperature during the CGL heat treatment to be 650 ° C. or more.
상기 Si은 강도상향에 유리한 원소이나 첨가량이 증가할수록 도금표면품질이 저하되는 문제점이 있으므로, 그 함량은 0.03%이하로 제한하는 것이 바람직하다.Since Si has a problem in that the plating surface quality decreases as an element or an added amount increases in strength, the content thereof is preferably limited to 0.03% or less.
상기 Mn은 고용강화 원소로서 C과 더불어 강도 확보 및 Ar3변태점을 저하 시키기 때문에 혼립조직 방지에 유리하고 소지철의 고강도 및 적정 연성확보를 위하여 첨가되는 성분으로서, 그 첨가량은 0.8∼1.0%로 제한하는 것이 바람직하다.Since Mn is a solid solution strengthening element, together with C, it secures strength and lowers Ar 3 transformation point, which is advantageous in preventing mixed structures and added to secure high strength and proper ductility of ferrous iron, and the amount thereof is limited to 0.8 to 1.0%. It is desirable to.
상기 Mn의 함량이 1.0% 초과하는 경우에는 제조원가가 높아지고 연성확보 및 냉간압연 부하가 발생하고, 0.8% 미만인 경우에는 충분한 강도확보가 곤란하다. If the Mn content exceeds 1.0%, manufacturing cost is high and ductility and cold rolling load are generated. If the Mn content is less than 0.8%, it is difficult to secure sufficient strength.
상기 P는 석출강화 원소로서 강도를 확보하기 위하여 첨가되는 성분으로서, 그 함량은 0.08~0.1%로 제한하는 것이 바람직하다.P is a component added to secure strength as a precipitation strengthening element, and its content is preferably limited to 0.08 to 0.1%.
일반적으로 P가 높아지면 편석 및 2차가공취성 문제가 있어 가공성이 저하되나 본 발명에서는 이러한 문제점을 해결하기 위하여 B이 5-15ppm 첨가된다.In general, when P is high, there is segregation and secondary processing brittleness problems, so that workability is lowered, but in the present invention, 5-15 ppm of B is added to solve such problems.
단순절곡 가공 및 90도 가공만을 하는 경우에는 편석 및 2차가공취성은 크게 문제되지 않는다.For simple bending and 90 degree machining, segregation and secondary processing brittleness are not a big problem.
상기 S는 강중 불순물로서 강중에 불가피하게 존재 하나 성분함량이 높으면 가공성에 나쁜 영향을 미치므로 0.015% 이하로 한정하는 것이 바람직하다. Although S is inevitably present in steel as an impurity in steel, it is preferable to limit it to 0.015% or less because high component content adversely affects workability.
상기 Al은 강의 탈산에 필요한 원소로서, 본 발명에서는 탈산에 필요한 통상 수준인 0.02∼0.06%로 한정한다.Al is an element necessary for deoxidation of steel, and is limited to 0.02% to 0.06% which is a normal level required for deoxidation in the present invention.
상기 Ti은 탄질화물 형성원소로서 CGL 재결정온도를 높혀주며, 또한 강도상승에도 유리하게 작용하므로, 제조원가 등을 고려하여 그 함량은 0.04~0.06%로 제한하는 것이 바람직하다.Ti is a carbonitride-forming element, which increases the CGL recrystallization temperature, and also advantageously increases the strength, so that the content is preferably limited to 0.04 to 0.06% in consideration of manufacturing cost.
상기 B은 고객사 최종가공후 2차 취성파괴 문제점을 해결하기 위해 첨가되는 성분으로서, 그 함량은 5~15ppm으로 제한하는 것이 바람직한데, 그 이유는 상기 B의 함량이 너무 적으면 첨가효과가 미비하고, 15ppm을 초과할 경우에는 원가가 증가하고 재질 이방성이 커지기 때문이다. The B is a component added to solve the secondary brittle fracture problem after the final processing of the customer, it is preferable to limit the content to 5 ~ 15ppm, because if the content of the B is too small the addition effect is insufficient In the case of exceeding 15 ppm, the cost increases and the material anisotropy increases.
이하, 본 발명의 제조조건에 대하여 설명한다.Hereinafter, the manufacturing conditions of this invention are demonstrated.
본 발명에 따라 용융아연도금강판을 제조하기 위해서는 본 발명의 강 슬라브를 열연 가열로에서 1150~1250℃ 정도로 가열한다.In order to manufacture the hot-dip galvanized steel sheet according to the present invention, the steel slab of the present invention is heated to about 1150 ~ 1250 ℃ in a hot-rolled heating furnace.
상기 슬라브의 가열온도(추출온도)가 높을 경우 열연강판 표면에 스케일이 많이 생성되어 표면품질을 저해하고, 1150℃이하일 경우에는 Ar3변태점 이상 온도 확보가 곤란하고 또한 고강도 2.3mm 이하 박물재의 압연부하를 초래하는 문제점이 발생한다.When the heating temperature (extraction temperature) of the slab is high, many scales are generated on the surface of the hot rolled steel sheet to hinder the surface quality, and when the temperature is lower than 1150 ° C, it is difficult to secure the temperature above the Ar 3 transformation point and the rolling load of the high strength 2.3 mm or less material Problems arise.
상기와 같이 가열된 슬라브를 Ar3변태점 이상인 880~940℃의 열간압연마무리온도조건으로 열간압연한 후 580∼650℃에서 저온권취를 실시한다,The slab heated as described above is hot rolled under the hot rolling finishing condition of 880-940 ° C. above Ar 3 transformation point, and then cold-rolled at 580-650 ° C.,
상기 열간압연공정은 열연강판의 두께가 2.1∼4.5mm가 되도록 행하는 것이 바람직하다.The hot rolling step is preferably performed so that the thickness of the hot rolled steel sheet is 2.1 to 4.5 mm.
일반적으로 열연강판은 권취온도가 높아질수록 강도가 저하되는 경향을 보이는데, 권취온도가 650℃를 초과할 경우 소지철의 결정립 온도가 커져 충분한 강도확보가 곤란하고, 권취온도가 580℃ 이하인 경우에는 입자가 지나치게 세립화되어 강도가 상승하고 산세 및 냉간압연공정(PCM)에서의 냉간압연 부하가 발생되므로, 열연강판의 권취온도는 580∼650℃로 제한하는 것이 바람직하다.In general, hot-rolled steel sheet tends to decrease in strength as the coiling temperature increases. If the coiling temperature exceeds 650 ° C, grain size of the base iron increases, making it difficult to secure sufficient strength, and when the coiling temperature is 580 ° C or less, Since the fine grains are excessively fined, the strength is increased, and the cold rolling load is generated in the pickling and cold rolling process (PCM), the winding temperature of the hot rolled steel sheet is preferably limited to 580 to 650 ° C.
즉, 580∼650℃의 권취온도구간에서 안정적이고 높은강도를 얻을 수 있다. That is, stable and high strength can be obtained in the winding temperature range of 580-650 degreeC.
다음에, 상기와 같이 제조된 열연강판을 산세하여 열연스케일을 제거한 후, 목표두께로 냉간압연한 다음, 탈지후, 650~700℃로 가열한 다음, 440~465℃로 냉각한 후, 용융아연도금욕에서 도금한 후, 0.7%이하의 연신율로 조질압연하여 용융아연도금강판을 제조한다.Next, the hot rolled steel sheet prepared as described above was removed to remove hot rolled scale, cold rolled to a target thickness, and then degreased, heated to 650 to 700 ° C., and then cooled to 440 to 465 ° C., followed by molten zinc. After plating in a plating bath, temper rolling at an elongation of less than 0.7% to produce a hot-dip galvanized steel sheet.
상기 탈지방법으로는 알카리탈지 또는 전해탈지방법등을 들수 있다.Examples of the degreasing method include alkaline degreasing or electrolytic degreasing.
CGL에서 인장강도 570MPa이상 구조용강 제조시 가장 중요한 것은 가능한 높은 열처리온도 범위에서 작업시에도 목표재질이 확보되어야 한다는 것이다. The most important thing in the production of structural steel with a tensile strength of 570 MPa or more in CGL is that the target material must be obtained even when working in the high heat treatment temperature range.
상기 열처리온도가 650℃ 미만인 경우에는 형상교정이 열위하고, 타 강종과 연결작업시 가열온도차이가 커서 로(Furnace) 및 작업성이 불안정하게 되는 문제점이 있다. If the heat treatment temperature is less than 650 ℃ shape correction is inferior, there is a problem that the furnace (workability) and workability is unstable because the difference in the heating temperature when connecting with other steel species.
그리고 저온열처리로 인한 형상을 개선하기 위해 열연코일두께를 하향하여 냉간압연할 경우 냉간압하율 하향으로 최종 제품 형상은 개선되나 열간마무리압연시 마무리압연 목표온도를 맞추기 위해 무리하게 가속압연을 행하여야 하는데, 이렇게 하는 경우에는 열간압연중 폭편차 발생 및 꼬임마크결함과 설비오동작이 발생하는 문제점이 있다.In order to improve the shape due to low temperature heat treatment, when cold rolling is performed by lowering the thickness of the hot rolled coil, the final product shape is improved by lowering the cold reduction rate, but it must be forcedly accelerated to meet the final rolling target temperature during hot finishing rolling. In this case, there is a problem in that the width deviation occurs during the hot rolling, the twist mark defect and the equipment malfunction occur.
따라서, 본 발명에서는 용융아연도금전의 열처리시 열처리온도를 650~700℃로 제한한 것이다.Therefore, in the present invention, the heat treatment temperature during the heat treatment before hot dip galvanizing is limited to 650 ~ 700 ℃.
상기 용융아연도금욕으로는 Al을 0.14∼0.25%, Pb 및 Sb을 각각 50ppm 이하 함유하고, 나머지 Zn 및 기타 불가피한 불순물로 조성되는 도금욕을 사용하는 것이 바람직하다.As the hot dip galvanizing bath, it is preferable to use a plating bath containing 0.14 to 0.25% of Al, 50 ppm or less of Pb and Sb, and composed of the remaining Zn and other unavoidable impurities.
CGI는 표면품질이 우수해야 하므로 피팅마크, 흐름무늬 및 생산후 3개월 경과후 강판표면이 검게 변하는 흑변현상이 없어야 한다. 일반적으로 Pb,Sb가 스팽글 입계에 존재하면 시간경과후 입계에 편석하여 경시 도금박리를 유발한다. Since CGI should have good surface quality, there should be no fitting mark, flow pattern, and blackening phenomenon that steel plate surface turns black after 3 months after production. In general, when Pb and Sb are present in the sequin grain boundary, it segregates in the grain boundary after elapse of time and causes delamination over time.
도금욕의 Pb, Sb성분이 포함되면 제로스팽글 제조를 위해 인산암모늄 용액 등을 분사하는데 분사자국이 피팅형태를 보임에 따라 표면 및 조도가 거칠어져 3개월 시간 경과후 또는 벤딩가공후 표면이 검게 변하게 된다. When Pb and Sb components of the plating bath are included, ammonium phosphate solution is sprayed to prepare the ZERO sequins. As the spray marks show the fitting shape, the surface and roughness become rough and the surface becomes black after 3 months or after bending. do.
따라서, 레귤러 스팽글 형성원소인 Pb, Sb 성분을 각각 50ppm 이하 함유하고, Al: 0.14∼0.25%, 나머지는 Zn 및 기타 불가피한 불순물로 조성되는 도금욕을 사용하여 용융아연도금하므로써 경시박리를 방지하고 그리고 표면품질을 개선하여 가공시에 경시 도금박리 및 흑변현상 등을 해결 하는 것이 바람직하다,Therefore, by using a plating bath containing 50 ppm or less of Pb and Sb components, which are regular sequin forming elements, with Al: 0.14 to 0.25% and the remainder being Zn and other unavoidable impurities, it is possible to prevent over time peeling and By improving the surface quality, it is desirable to solve the plating peeling and blackening phenomenon over time during processing.
한편, 본 발명에서는 용융아연강판에 적정한 조도를 부여하고 형상을 교정하기 위하여 스킨패스밀에서 0.7%이하의 연신율로 조질압연을 행하는 것이 바람직하다.On the other hand, in the present invention, it is preferable to perform temper rolling at an elongation of not more than 0.7% in a skin pass mill in order to impart proper roughness to the molten zinc steel sheet and to correct the shape.
상기 조질압연시 연신율이 0.7%를 초과하는 경우에는 작업불량이 발생하고 연신율이 저하된다.When the elongation at temper rolling exceeds 0.7%, a malfunction occurs and the elongation is lowered.
상기와 같이 본 발명에 따라 적절한 조성을 갖는 강슬라브를 적절한 조건으로 용융아연도금강판을 제조하므로써 형상, 표면 및 도금밀착성이 양호하고 고항복비형 고강도 구조용강으로서 적정연성을 확보하여 항복강도 560MPa이상, 인장강도 570MPa이상, 연신율 3% 이상의 KS,JIS 규격을 충족하고 종래 구조용강에 비하여 재질편차 및 불량이 적고 연성이 향상되고, 형상이 우수한 용융아연도금강판을 제조할 수 있다.According to the present invention, by manufacturing a hot-dip galvanized steel sheet under appropriate conditions with a steel slab having an appropriate composition, the shape, surface and plating adhesion are good, and the yield strength is high as a high yield ratio type high strength structural steel, yielding strength of 560 MPa or more and tensile strength. It can meet the KS, JIS standards of strength 570MPa or more, elongation of 3% or more, and can produce a hot-dip galvanized steel sheet having less material deviation and defects than the conventional structural steel, improving ductility, and excellent shape.
또한, 본 발명은 CGL 열처리온도 상향으로 작업성을 대폭 개선시킬 수 있다.In addition, the present invention can significantly improve the workability by raising the CGL heat treatment temperature.
이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.
(실시예)(Example)
하기 표 1과 같이 조성되는 강을 연주공정에서 슬라브로 제조한 후 1150∼1250℃ 범위에서 2시간 재가열 한 다음, 열간압연하여 열연강판을 제조하였다. 이때 열간 마무리온도는 910℃로 하였고, 권취온도는 하기 표 2에 나타낸 바와 같이 581∼645℃ 범위로 하였다. The steel prepared as shown in Table 1 was produced as a slab in the reproducing process, and then reheated for 2 hours in the range of 1150 ~ 1250 ℃, followed by hot rolling to prepare a hot rolled steel sheet. At this time, the hot finishing temperature was 910 ℃, the winding temperature was set to 581 ~ 645 ℃ range as shown in Table 2.
상기와 같이 제조된 열연강판을 산세,냉간압연공정에서 산세 및 목표두께로 냉간압연하여 풀하드코일(FULL HARD COIL)을 제조한다. 이 풀하드코일을 660~695℃로 가열후, 460℃로 냉각한 다음, 용융아연도금욕에 침적하여 도금하였다. The hot rolled steel sheet manufactured as described above is cold rolled to a pickling and a target thickness in a pickling and cold rolling process to produce a full hard coil. The full hard coil was heated to 660˜695 ° C., cooled to 460 ° C., and then plated by plating in a hot dip galvanizing bath.
상기 아연도금욕으로는 Pb, Sb 성분을 각각 30ppm, Al을 0.20%함유하고, 나머지는 Zn 및 기타 불가피한 불순물로 조성되는 용융아연욕을 사용하였다. As the zinc plating bath, a molten zinc bath containing 30 ppm of Pb and Sb components and 0.20% of Al, and the rest of which is composed of Zn and other unavoidable impurities was used.
그리고 강판의 적정 조도부여와 형상교정을 위해 스킨패스밀에서 0.25%의 연신율로 조질압연을 하였다. Then, temper rolling was carried out at a skin pass mill at an elongation of 0.25% for proper roughness and shape correction.
상기와 같이 제조된 강판에 대하여 항복강도, 인장강도, 연신율, 형상품질 및 작업성을 평가하고, 그 결과를 하기 표 2에 나타내었다.The yield strength, tensile strength, elongation, shape quality and workability of the steel sheet manufactured as described above were evaluated, and the results are shown in Table 2 below.
하기 표 1에서 종래강(1)은 저탄소강+ Ti강, 종래강(2)는 중저 +Ti강, 종래강(3)은 중탄소강, 종래강(4)는 극저+Ti강, 비교강(1)은 극저 P+Ti강, 비교강(2)는 극저+Mn+P+Ti강이며, 반면에 발명강은 극저+고Mn+고P+Ti+B첨가강이다In Table 1, conventional steel (1) is a low carbon steel + Ti steel, conventional steel (2) is a medium-low + Ti steel, conventional steel (3) is a medium carbon steel, conventional steel (4) is very low + Ti steel, comparative steel ( 1) is very low P + Ti steel, comparative steel (2) is very low + Mn + P + Ti steel, while invention steel is very low + high Mn + high P + Ti + B additive steel
상기 표 2에 나타난 바와 같이, 종래재(1~4)및 비교재(1~2)는 열처리온도를 620℃ 이하로 CGL열처리를 행하므로써, 재질 및 형상 각각이 불량하거나 또는 재질 및 형상 모두가 불량하거나 작업성이 불량함을 알 수 있다. As shown in Table 2, the conventional materials (1 to 4) and the comparative materials (1 to 2) are subjected to CGL heat treatment at a heat treatment temperature of 620 ° C. or lower, so that the materials and shapes are each poor or both the materials and shapes are poor. It can be seen that poor or poor workability.
반면에, 본 발명에 부합되는 발명재(1~3)의 경우에는 CGL 열처리온도가 상대적으로 높은 660~695℃에서 작업함에 따라 형상품질 및 작업성이 양호하며, 목표재질도 충족시키고 있음을 알 수 있다.On the other hand, in the case of the inventive materials (1 to 3) according to the present invention, the shape quality and workability are good as the CGL heat treatment temperature is relatively high at 660 to 695 ° C., and the target materials are also satisfied. Can be.
상기한 바와 같이, 본 발명에 의하면 데크플레이트, 스틸하우스 스터드(Stud), 천정보강재, 족장판 등에 사용되는 높은 항복강도(560MPa이상) 및 높은 인장강도 (570MPa이상)와 적정 가공성이 요구되는 CGI강판 제조시, 종래방법과 비교하여 재질편차, 재질불량, 형상불량을 대폭개선시킬 수 있고, 또한 작업성을 획기적으로 개선시킬 수 있다. As described above, according to the present invention, CGI steel sheet having high yield strength (560 MPa or more), high tensile strength (570 MPa or more), and appropriate workability, used for deck plates, steel house studs, fabric steels, and chief plates. In manufacturing, compared with the conventional method, material deviation, material defect, and shape defect can be greatly improved, and workability can be significantly improved.
또한, 본 발명에 의하면, 향후 고객사에게 CGI 고강도 구조용강을 공급 할 수 있게 되어 고객사 원가절감에 기여하고, 자원 및 에너지를 절감할 수 있다.In addition, according to the present invention, it is possible to supply CGI high-strength structural steel to the customer in the future to contribute to the cost reduction of the customer, it is possible to save resources and energy.
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KR100705243B1 (en) * | 2005-07-20 | 2007-04-10 | 현대하이스코 주식회사 | Hot dip galvanized steel sheets of TRIP steels which have good adhesion property and excellent formability and the method of developing those steels |
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JPH05230614A (en) * | 1992-02-21 | 1993-09-07 | Nkk Corp | Manufacture of high strength hot dip calvanized steel sheet for deep drawing |
JPH0657337A (en) * | 1992-08-10 | 1994-03-01 | Nippon Steel Corp | Production of high strength galvannealed steel sheet excellent in formability |
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KR20010085282A (en) * | 1999-02-22 | 2001-09-07 | 아사무라 타카싯 | High strength galvanized steel plate excellent in adhesion of plated metal and formability in press working and high strength alloy galvanized steel plate and method for production thereof |
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JPH05230614A (en) * | 1992-02-21 | 1993-09-07 | Nkk Corp | Manufacture of high strength hot dip calvanized steel sheet for deep drawing |
JPH0657337A (en) * | 1992-08-10 | 1994-03-01 | Nippon Steel Corp | Production of high strength galvannealed steel sheet excellent in formability |
KR960702013A (en) * | 1994-02-15 | 1996-03-28 | 도사끼 시노부 | High tensile alloyed hot dip galvanized steel sheet with excellent plating characteristics and manufacturing method thereof |
WO1996002013A1 (en) * | 1994-07-12 | 1996-01-25 | Coherent, Inc. | Optical system for improving the symmetry of the beam emitted from a broad area laser diode |
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