KR20020042154A - method of manufacturing melting galvanized steel iron with good workability and chipping resistance - Google Patents
method of manufacturing melting galvanized steel iron with good workability and chipping resistance Download PDFInfo
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- KR20020042154A KR20020042154A KR1020000071934A KR20000071934A KR20020042154A KR 20020042154 A KR20020042154 A KR 20020042154A KR 1020000071934 A KR1020000071934 A KR 1020000071934A KR 20000071934 A KR20000071934 A KR 20000071934A KR 20020042154 A KR20020042154 A KR 20020042154A
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 24
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 24
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title description 27
- 229910052742 iron Inorganic materials 0.000 title description 13
- 238000002844 melting Methods 0.000 title 1
- 230000008018 melting Effects 0.000 title 1
- 238000010438 heat treatment Methods 0.000 claims abstract description 39
- 230000006698 induction Effects 0.000 claims abstract description 27
- 238000000034 method Methods 0.000 claims abstract description 15
- 238000005275 alloying Methods 0.000 claims description 36
- 238000001816 cooling Methods 0.000 claims description 28
- 238000005246 galvanizing Methods 0.000 claims description 7
- 239000003595 mist Substances 0.000 claims description 6
- 229910000831 Steel Inorganic materials 0.000 abstract description 11
- 239000010959 steel Substances 0.000 abstract description 11
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 abstract description 9
- 239000011701 zinc Substances 0.000 abstract description 9
- 229910052725 zinc Inorganic materials 0.000 abstract description 9
- 230000015271 coagulation Effects 0.000 abstract 1
- 238000005345 coagulation Methods 0.000 abstract 1
- 238000002425 crystallisation Methods 0.000 abstract 1
- 230000008025 crystallization Effects 0.000 abstract 1
- 230000005611 electricity Effects 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 37
- 238000000227 grinding Methods 0.000 description 18
- 238000007747 plating Methods 0.000 description 17
- 230000000052 comparative effect Effects 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 10
- 239000000956 alloy Substances 0.000 description 10
- 229910000905 alloy phase Inorganic materials 0.000 description 10
- 239000011248 coating agent Substances 0.000 description 7
- 238000000576 coating method Methods 0.000 description 7
- 238000009792 diffusion process Methods 0.000 description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 4
- 229910019142 PO4 Inorganic materials 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 238000004070 electrodeposition Methods 0.000 description 3
- 230000001050 lubricating effect Effects 0.000 description 3
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 3
- 239000010452 phosphate Substances 0.000 description 3
- 230000001629 suppression Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- VZSRBBMJRBPUNF-UHFFFAOYSA-N 2-(2,3-dihydro-1H-inden-2-ylamino)-N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]pyrimidine-5-carboxamide Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C(=O)NCCC(N1CC2=C(CC1)NN=N2)=O VZSRBBMJRBPUNF-UHFFFAOYSA-N 0.000 description 1
- YLZOPXRUQYQQID-UHFFFAOYSA-N 3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]propan-1-one Chemical compound N1N=NC=2CN(CCC=21)CCC(=O)N1CCN(CC1)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F YLZOPXRUQYQQID-UHFFFAOYSA-N 0.000 description 1
- DEXFNLNNUZKHNO-UHFFFAOYSA-N 6-[3-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperidin-1-yl]-3-oxopropyl]-3H-1,3-benzoxazol-2-one Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1CCN(CC1)C(CCC1=CC2=C(NC(O2)=O)C=C1)=O DEXFNLNNUZKHNO-UHFFFAOYSA-N 0.000 description 1
- 241000208340 Araliaceae Species 0.000 description 1
- MKYBYDHXWVHEJW-UHFFFAOYSA-N N-[1-oxo-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propan-2-yl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(C(C)NC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 MKYBYDHXWVHEJW-UHFFFAOYSA-N 0.000 description 1
- 229910001096 P alloy Inorganic materials 0.000 description 1
- 235000005035 Panax pseudoginseng ssp. pseudoginseng Nutrition 0.000 description 1
- 235000003140 Panax quinquefolius Nutrition 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009529 body temperature measurement Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 235000008434 ginseng Nutrition 0.000 description 1
- 230000009036 growth inhibition Effects 0.000 description 1
- 230000003116 impacting effect Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- DPTATFGPDCLUTF-UHFFFAOYSA-N phosphanylidyneiron Chemical compound [Fe]#P DPTATFGPDCLUTF-UHFFFAOYSA-N 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Classifications
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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
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B05—SPRAYING OR ATOMISING IN GENERAL; APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
- B05D—PROCESSES FOR APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
- B05D3/00—Pretreatment of surfaces to which liquids or other fluent materials are to be applied; After-treatment of applied coatings, e.g. intermediate treating of an applied coating preparatory to subsequent applications of liquids or other fluent materials
- B05D3/007—After-treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
- C22C18/04—Alloys based on zinc with aluminium as the next major constituent
-
- 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
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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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
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Physics & Mathematics (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Thermal Sciences (AREA)
- Coating With Molten Metal (AREA)
Abstract
Description
본 발명은 고주파 유도가열로에 의한 합금화 용융아연 도금열처리시 유도가열로의 출력비를 2:1∼4:1로 조절하여 급속가열하고, 합금화 열처리후 30∼50℃/초로 급속냉각함으로써 가공성 및 내치핑성이 우수한 합금화 용융아연 도금강판의 제조방법으로, 보다 상세하게는 Al농도 0.13∼0.14wt%인 용융아연 도금욕에서 인양한 아연도금 강판이 응고되기 전에 고주파 유도가열로의 하부 존과 상부 존의 출력비를 2:1∼4:1로 급속가열하여 제타상 및 감마상의 성장을 억제하고, 에어 미스트를 사용하여 30∼50℃/초로 급속냉각하여 취약한 감마상의 성장을 억제함으로써 도금층의 가공성 및 내치핑성을 향상시킨 합금화 용융아연 도금강판의 제조방법이다.합금화 용융아연 도금강판은 내식성, 도장성 및 용접성이 우수하면서 가격이 저렴하여 최근 일본, 미국을 중심으로 자동차 외판용도로 사용이 확대되고 있다. 이러한 특성은 합금화 용융아연 도금강판의 아연과 철의 합금화 도금층에 의해 나타나는 것이다. 합금화 도금층은 연속용융도금 공정중에서 용융아연욕조를 통과한 후아연 도금된 강판을 표층의 아연도금층이 완전히 굳기 전에 직상부에 설치된 합금화 열처리로에서 도금층을 가열한 후 공기냉각대에서 급속 냉각시켜 제조하게 된다.The present invention is a rapid heating by adjusting the output ratio of the induction heating furnace 2: 1 to 4: 1 during the alloying hot dip galvanizing heat treatment by the high frequency induction heating furnace, and by rapid cooling to 30 ~ 50 ℃ / sec after the alloying heat treatment A method for producing an alloyed hot-dip galvanized steel sheet having excellent chipping properties. More specifically, a lower zone and an upper zone of a high frequency induction furnace before solidifying a galvanized steel plate lifted in a hot dip galvanizing bath having an Al concentration of 0.13 to 0.14 wt%. The ratio of the output power is 2: 1 to 4: 1 for rapid heating to suppress the growth of the zeta phase and the gamma phase and the rapid cooling to 30 to 50 ° C / sec using the air mist to suppress the growth of the weak gamma phase. It is a manufacturing method of alloyed hot-dip galvanized steel sheet with improved chipping property. Since alloyed hot-dip galvanized steel sheet has excellent corrosion resistance, paintability and weldability, and is low in price, Has been expanded using a car shell uses a shim. This property is exhibited by an alloy plating layer of zinc and iron of an alloyed hot dip galvanized steel sheet. The alloyed plating layer is manufactured by passing the hot dip galvanized bath in the continuous hot dip plating process and heating the plated layer in an alloy heat treatment furnace installed in the upper part before the zinc plated layer of the surface layer is completely hardened, followed by rapid cooling in an air cooling zone. do.
이러한 합금화 열처리시 용융상태의 아연과 소지의 철성분이 열확산 반응으로 합금층을 생성시키게 되고 상온으로 냉각됨에 따라 그 반응은 중지하게 된다. 합금화 용융아연 도금층에 존재하는 각상과 그 특성을 설명하면 먼저 소지철과의 계면에 존재하는 케피탈 감마(Γ)상과 케피탈 감마원(Γ1)상은 각각 합금층중 철 성분의 함량이 24∼31wt% 및 18.5∼23.5wt%이고, 금속학적 격자 구조는 체심 입방정계와 면심입방정계이다. 이중 케피탈 감마상이 가장 취약한 상으로서, 가공시 합금층의 파우더링(Powdering)을 발생시키는 주요인이다. 다음으로 그 상층에 존재하는 델타상(δ)은 철성분이 8.5∼13wt%이고 육방 정계로 격자 구조가 되어 있어 케피탈 감마층에 비해 가공성이 우수하며 또한 마찰계수가 낮다. 제일 상층에 존재하는 제타(ζ)상은 철성분이 6.7∼7.2wt%이고, 격자 구조가 단사정계로 이루어져 있어 합금상중 가공성은 가장 좋으나 마찰계수가 높아 가공시 합금층의 플래킹(Flaking)현상을 유발하게 된다. 따라서 가공성 측면에서 감마상과 제타상이 매우 얇고 델타상으로만 형성된 합금상을 갖는 것이 유리하다. 또한 자동차사에서 전착도장후 고속으로 자갈등을 충돌시켜 도금층이 탈락되는 정도를 평가하는 치핑성(Stone chipping)도 감마상 및 제타상을 최소화시켜야 향상된다. 그러나 이러한 합금상들은 열 확산에 의해 도금층중의 아연과 소지의 철성분이 합금화 반응을 일으켜 생성되는 것으로 강성분, 합금화처리 온도, 합금화 처리시간 및 용융아연도금욕중의 성분에 따라 합금상들의 분포가 달라지게 된다.During such an alloying heat treatment, the zinc in the molten state and the base iron are thermally diffused to form an alloy layer, and the reaction is stopped as it is cooled to room temperature. The phases present in the alloyed hot-dip galvanized layer and the characteristics thereof will be described. First, the kepital gamma (Γ) phase and the kepital gamma source (Γ1) phase present at the interface with the base iron have a content of 24 to 31 wt% of iron in the alloy layer, respectively. And 18.5 to 23.5 wt%, and the metallic lattice structure is a body centered cubic system and a face centered cubic system. Among them, the capital Gamma phase is the weakest phase and is the main cause of powdering of the alloy layer during processing. Next, the delta phase (δ) present in the upper layer has an iron component of 8.5 to 13 wt% and has a hexagonal lattice structure, which is superior in workability and low coefficient of friction as compared to the capacitive gamma layer. The zeta (ζ) phase present in the uppermost layer has the iron component of 6.7-7.2wt% and the lattice structure consists of monoclinic system, which has the best workability among the alloy phases, but has a high coefficient of friction. Will cause. Therefore, in view of workability, it is advantageous to have an alloy phase in which the gamma phase and the zeta phase are very thin and formed only in the delta phase. In addition, chip chipping, which evaluates the degree of plating layer dropping by colliding gravel at high speed after electrodeposition coating, is improved by minimizing gamma and zeta phase. However, these alloy phases are produced by thermal diffusion of zinc in the plating layer with the iron component of the base material. The distribution of the alloy phases according to the steel composition, alloying temperature, alloying time, and components in the hot dip galvanizing bath is performed. Will be different.
기존의 버너(Burner)를 이용한 직화가열 방식에 의한 합금화 열처리는 도금강판의 온도분포가 불균일하고 급속가열이 어려워 제타상 또는 감마상이 두껍게 형성되는 문제점이 많이 발생하였다. 따라서 최근에 고주파 또는 저주파 유도가열 방식에 의한 합금화 열처리 방식을 채택한 결과 온도분포가 균일하여 합금상제어가 용이한 잇점이 있는 것으로 보고되고 있다. 그러나 유도가열로의 출력비 및 합금화처리 조건이 부적절하면 가공성 및 내치핑성이 열화되는 문제점이 상존하였다. 따라서 본 발명에서는 유도가열로의 출력비 및 합금화처리후 냉각속도를 조절하여 가공성 및 내치핑성이 우수한 합금화 용융아연 도금강판을 제조하고자 하였다.Alloying heat treatment by the direct heating method using a conventional burner has a lot of problems in that the temperature distribution of the plated steel sheet is uneven and rapid heating is difficult to form a thick zeta or gamma phase. Therefore, recently, as a result of adopting the alloying heat treatment method by the high frequency or low frequency induction heating method, it is reported that the temperature distribution is uniform and the alloy phase control is easy. However, when the output ratio of the induction furnace and the alloying conditions are inadequate, the problem of deterioration of workability and chipping resistance has existed. Therefore, in the present invention, an alloyed hot-dip galvanized steel sheet excellent in workability and chipping resistance was prepared by controlling the output ratio of the induction furnace and the cooling rate after the alloying treatment.
종래의 합금화 용융아연 도금강판의 가공성을 향상시키기 위한 방법으로 일본 신일철(NSC)에서는 합금화 용융아연 도금층 상부에 얇게 철을 전기도금한 플레쉬(Flash) 합금화 용융아연 도금강판을 생산하여 왔다. 또한 일본 가와사키(KSC)에서는 철-인 합금도금을 플레쉬 도금한 합금화 용융아연 도금강판을 개발하였다. 그러나 자동차사의 원가절감 요구에 따라 미국 LTV에서 소량 생산하고 있는 인산염처리 합금화 용융아연 도금강판 및 일본 강관(NKK)의 니켈계 무기윤활 피복강판 등이 개발되었다.As a method for improving the processability of conventional alloyed hot-dip galvanized steel sheet (NSC) has produced a flash alloyed hot-dip galvanized steel sheet with a thin electroplated iron on the alloyed hot-dip galvanized layer. In addition, Kawasaki, Japan (KSC) has developed an alloyed hot-dip galvanized steel sheet that is flash-plated with iron-phosphorus alloy plating. However, in response to the cost reduction demands of automobile companies, phosphate-treated alloyed hot-dip galvanized steel sheets produced by US LTV and nickel-based inorganic lubricated coated steel sheets of NKK were developed.
전자는 합금화 용융도금 강판위에 인산염 피막(Zn3-xMx(PO4)2·4H2O)를 0.5∼1g/m2 도포시켜 프레스 가공시 성형하중 감소로 프레스 다이의 수명연장 및 마찰계수 감소로 가공성은 향상되나, 파우더링성이 열화되고 자동차사의 전착도장시 전처리공정에서 인산염피막이 잘 탈지가 되지 않아 도장밀착성이 열화되는 문제점이있다. 후자는 합금화 용융도금 강판 위에 니켈계 윤활피막을 100∼200mg/m2 도포시킨 것으로 마찰계수를 감소하여 프레스 성형성이 개선되고 인산염처리성, 도장성, 내식성은 일반 합금화 용융아연 도금강판과 동등한 성능을 갖는 것으로 보고되고 있다. 그러나 별도의 윤활피막을 도포할 수 있는 설비신설이 필요하고 제조원가가 상승하므로 자동차 사에서 거의 채택하고 있지 않고 있다. 또한 코러스(Corrus)에서는 강성분에 Si를 소량 첨가하면, 도금층과 소지철사이의 결합력을 증가시켜 내치핑성이 향상한다고 발표하였으나, 본 연구자의 실험결과 Si첨가시 합금화가 크게 억제되는 문제점이 나타났다.The former is coated with 0.5 ~ 1g / m2 of phosphate film (Zn3-xMx (PO4) 2 · 4H2O) on the alloyed hot-dip steel sheet, which improves workability by reducing the molding load during press work and extending the life of the press die and reducing the friction coefficient. There is a problem in that the powdering property is deteriorated and the coating adhesion is deteriorated because the phosphate coating is not degreased well in the pretreatment process during the electrodeposition coating of automobiles. The latter is 100 ~ 200mg / m2 nickel coated lubricating coating on alloyed hot-dip galvanized steel sheet, which reduces the coefficient of friction and improves press formability. It is reported to have. However, it is rarely adopted by automobile companies due to the necessity of new facility to apply a separate lubricating film and the increase of manufacturing cost. In addition, although a small amount of Si was added to the steel component in Corrus, it was found that the chipping resistance was improved by increasing the bonding force between the plated layer and the base iron, but the experimental results showed that the alloying was greatly suppressed when Si was added.
본 발명은 상기와 같은 문제점을 해결하기 위하여 안출된 것으로서, 위에서 기술한 별도의 플레쉬도금, 인삼염처리, 윤활피복 등의 후처리 및 강성분 변경없이 가공성 및 내치핑성이 우수한 합금화 용융아연 도금강판을 제조할 수 있는 방법을 개발하고자 하였다. 특히 본 발명자는 합금화 용융아연 도금층내 합금상분포가 합금화 초기의 열처리조건 및 합금화처리후 냉각속도에 따라 크게 변화되고, 이에 따라 도금층의 가공성 및 내치핑성이 크게 영향받는 것을 수많은 반복실험 및 각종 품질평가를 통해 밝혀내었다.The present invention has been made to solve the above problems, alloying hot-dip galvanized steel sheet excellent in workability and chipping resistance without the after-treatment and steel composition of the separate flash plating, ginseng treatment, lubricating coating, etc. described above An attempt was made to develop a method for preparing the same. In particular, the inventors found that the alloy phase distribution in the alloyed hot-dip galvanized layer is greatly changed according to the heat treatment conditions and the cooling rate after the initial alloying process, and thus the workability and chipping resistance of the plated layer are greatly affected. The evaluation revealed it.
본 발명은 고주파 유도가열로에 의한 합금화 용융아연 도금열처리시 유도가열로의 출력비를 2:1∼4:1로 조절하여 급속가열하고, 합금화 열처리후 30∼50℃/초로 급속냉각함으로써 가공성및 내치핑성이 우수한 합금화 용융아연 도금강판의 제조방법이다. 보다 상세하게는 Al농도 0.13∼0.14wt%인 용융아연 도금욕에서 인양한아연도금 강판이 응고되기 전에 고주파 유도가열로의 하부 존과 상부 존의 출력비를 2:1∼4:1로 급속가열하여 제타상 및 감마상의 성장을 억제하고, 에어 미스트를 사용하여 30∼50℃/초로 급속냉각하여 취약한 감마상의 성장을 억제함으로써 도금층의 가공성 및 내치핑성을 향상시킨 합금화 용융아연 도금강판의 제조방법을 제공하는 것을 목적으로 한다.The present invention is rapid heating by adjusting the output ratio of the induction heating furnace 2: 1 to 4: 1 during the alloying hot dip galvanizing heat treatment by the high frequency induction heating furnace, by rapid cooling to 30 ~ 50 ℃ / sec after alloy heat treatment It is a method for producing an alloyed hot dip galvanized steel sheet having excellent chipping properties. More specifically, before the solidified zinc plated steel sheet is solidified in a hot dip galvanizing bath having an Al concentration of 0.13 to 0.14 wt%, the output ratio of the lower zone and the upper zone of the high frequency induction furnace is rapidly heated to 2: 1 to 4: 1. A method for producing an alloyed hot-dip galvanized steel sheet which suppresses the growth of the zeta phase and the gamma phase and suppresses the growth of the vulnerable gamma phase by rapid cooling at 30 to 50 ° C./sec using an air mist. It aims to provide.
이하 본 발명을 더욱 상세히 설명하기로 한다.Hereinafter, the present invention will be described in more detail.
강판이 도금욕에서 합금화로에 들어가기 전에 Fe2Al5 합금층이 형성된다. 이들 초기 합금층들은 완전한 합금층을 형성하기 위한 철-아연 변태를 지연하기 때문에 확산억제층(inhibition layer)으로 불리고 있다. 이들 확산억제층은 합금화처리시 불안정하게 되어 완전한 철-아연 합금층을 형성하게 된다. 이때 초기 합금화 가열속도가 빠르면 확산억제층이 빠르게 소멸되고, 제타상의 성장이 억제되는 반면, 가열속도가 느리면 초기 합금화반응은 아웃버스트(outburst)형태로 불균일하게 일어난다. 또한 저온에서 안정한 제타상의 성장이 촉진되어 플레킹성이 저하된다. 또한 합금화 열처리후 냉각속도가 10∼25℃/초로 느리면, 취약한 감마상의 성장이 촉진되어 파우더링성 및 내치핑성이 크게 열화되는 문제점이 나타났다.The Fe 2 Al 5 alloy layer is formed before the steel sheet enters the alloying furnace in the plating bath. These initial alloy layers are called diffusion inhibition layers because they delay the iron-zinc transformation to form a complete alloy layer. These diffusion inhibitory layers become unstable during the alloying process to form a complete iron-zinc alloy layer. At this time, if the initial alloying heating rate is high, the diffusion suppression layer is quickly extinguished, and the growth of the zeta phase is suppressed. On the other hand, if the heating rate is low, the initial alloying reaction occurs unevenly in the form of outburst. In addition, growth of the zeta phase that is stable at low temperatures is promoted, and flaking properties are lowered. In addition, if the cooling rate after the alloying heat treatment is slow to 10 ~ 25 ℃ / second, the growth of the vulnerable gamma phase is promoted, the powdering resistance and chipping resistance was greatly deteriorated.
본 발명에서 고주파 유도가열로의 하부 존과 상부 존의 출력비를 2:1∼4:1로 한정한 이유에 대해 설명한다.The reason for limiting the output ratio of the lower zone and the upper zone of the high frequency induction furnace in the present invention is 2: 1 to 4: 1.
통상적인 합금화 열처리로는 가열대(heating), 균열대(soaking) 및 냉각대(cooling)로 구성되어 있다. 유도가열방식에 의한 가열대는 여러 개의 유도가열로로 구성되기도 하나, 통상적인 가열로는 하부 및 상부 존의 2개의 유도가열로로 구성되어 있다. 합금화 용융아연 도금강판의 합금화 온도는 아연도금강판의 방사율의 편차가 심하여 정확한 온도측정이 곤란하기 때문에 통상 유도가열로의 출력으로 조절하고 있다.Conventional alloying heat treatment furnaces consist of heating, soaking and cooling. The heating table by the induction heating method is composed of several induction heating furnaces, but a conventional heating furnace is composed of two induction heating furnaces of a lower zone and an upper zone. The alloying temperature of the alloyed hot-dip galvanized steel sheet is usually controlled by the output of the induction furnace because the emissivity of the galvanized steel sheet is so severe that accurate temperature measurement is difficult.
따라서 본 발명에서는 균열대에 인입하기전의 유도가열로에서 합금화 초기 및 후기의 가열속도를 차별화하여 제타상 및 감마상의 성장을 억제하고자 하였다. 균열대에 인입하기 전의 하부존의 유도가열 출력이 상부존에 비해 적거나나 2:1 미만이면, 초기 확산억제층의 파괴가 불균일하게 이루어지고 아웃버스트 조직이 발달하며, 제타상이 두껍게 성장하여 최종 합금층은 제타상이 주성분이며 프레스 가공시 마찰계수가 증가되고, 소지철과 도금층 계면에서 플레이킹 형태로 도금층이 탈락되는 문제점이 발생하였다. 한편 하부존의 유도가열 출력이 4:1를 초과한 경우는 과도한 합금화로 인해 감마상이 두껍게 성장하여 내파우더링성 및 내치핑성이 저하되고 전자기적인 충돌로 인해 유도가열로의 셧다운(Shut down)이 많이 나타났다. 그러나 본 발명의 하부 존과 상부 존의 출력비를 2:1∼4:1로 조절하면, 확산억제층이 빠르게 소멸되고, 제타상 및 감마상의 성장이 억제되어 도금층의 가공성 및 내치핑성이 크게 향상되었다.Therefore, in the present invention, it was intended to suppress the growth of the zeta phase and the gamma phase by differentiating the initial heating rate and the late heating rate in the induction heating furnace before entering the crack zone. If the induction heating output of the lower zone before entering the cracking zone is less than 2: 1 or less than the upper zone, the initial diffusion inhibiting layer is unevenly destroyed, the outburst structure is developed, and the zeta phase grows thick, resulting in the final alloy. The layer has a zeta phase as a main component, and the friction coefficient is increased during press working, and the plating layer is dropped in the form of flaking at the interface between the base iron and the plating layer. On the other hand, if the induction heating output of the lower zone exceeds 4: 1, the gamma image grows thick due to excessive alloying, and the powdering resistance and the chipping resistance are degraded, and the shutdown of the induction furnace due to the electromagnetic collision is caused. Appeared a lot. However, when the output ratio of the lower zone and the upper zone of the present invention is adjusted to 2: 1 to 4: 1, the diffusion suppression layer is quickly extinguished, the growth of the zeta phase and the gamma phase is suppressed, and the workability and chipping resistance of the plating layer are greatly improved. It became.
다음은 합금화처리후 냉각속도를 30∼50℃/초로 한정한 이유에 대해 설명한다. 합금화처리후 냉각속도가 30℃/초 미만이면, 냉각과정중에 합금화가 진행되어 취약한 감마상이 두껍게 성장하여 파우더링성 및 내치핑성이 크게 열화되었다. 반면 냉각속도를 50℃/초 이상으로 하는 것은 에어 미스트 방법으로는 곤란하였으며, 취약한 감마상 성장억제 증대효과도 없는 것으로 나타났다.Next, the reason why the cooling rate after the alloying treatment is limited to 30 to 50 ° C / sec will be explained. If the cooling rate after the alloying treatment is less than 30 ℃ / seconds, the alloying proceeds during the cooling process, the weak gamma phase grows thick, greatly deteriorated powdering and chipping resistance. On the other hand, it was difficult to increase the cooling rate above 50 ° C / sec by the air mist method, and there was no effect of increasing the growth inhibition of the weak gamma phase.
이밖에 도금욕내 알루미늄 농도는 0.13∼0.14%로 한정하는 것이 필요하다. 도금욕내 Al농도가 0.13%미만인 경우, 취약한 감마상의 형성을 촉진하여 파우더링량이 크게 증가하였다. 반면 알루미늄 농도가 0.14%를 초과하면 초기 확산억제층이 두껍게 형성되어 철-아연간의 합금화반응이 매우 억제되기 때문에 제타상으로 이루어진 미합금화 아연도금층을 형성하여 내플레킹성이 열화되었다.In addition, the aluminum concentration in the plating bath needs to be limited to 0.13 to 0.14%. When the Al concentration in the plating bath was less than 0.13%, the amount of powdering was greatly increased by promoting formation of a weak gamma phase. On the other hand, when the aluminum concentration exceeds 0.14%, the initial diffusion suppression layer is formed thick, and the alloying reaction between iron and zinc is very suppressed, thereby forming an unalloyed zinc plating layer composed of zeta phase, thereby deteriorating the flaking resistance.
내파우더링성 및 내치핑성은 합금상중의 감마상 두께에 밀접한 관계가 있다. 특히 감마상 두께를 0.5㎛미만으로 관리하는 것이 내파우더링성 및 내치핑성 측면에서 필요하며, 합금상중의 감마상 두께와 합금화도 간의 상관 관계를 조사한 결과, 480∼500℃의 저온에서 장시간 합금화처리하여 합금화도(도금층내 철함량)을 9∼11wt%로 좁게 관리시 0.6㎛ 미만의 감마상 두께를 얻을 수 있다. 즉 합금화도가 9wt% 미만에서는 주로 제타상으로 이루어진 합금상으로 플레이킹 발생이 증가하며, 11wt%를 초과시에는 감마상 두께가 0.6㎛를 초과하여 내파우더링성 및 내치핑성이 저하된다.Powder resistance and chipping resistance are closely related to the thickness of the gamma phase in the alloy phase. In particular, it is necessary to manage the gamma phase thickness to be less than 0.5 μm in terms of powder resistance and chipping resistance, and as a result of investigating the correlation between the gamma phase thickness and the alloying degree in the alloy phase, the alloying treatment is performed at a low temperature of 480 to 500 ° C. for a long time. When the alloying degree (iron content in the plating layer) is narrowly controlled to 9 to 11 wt%, a gamma-phase thickness of less than 0.6 µm can be obtained. That is, when the alloying degree is less than 9wt%, flaking occurs to the alloy phase mainly composed of zeta phase, and when it exceeds 11wt%, the gamma phase thickness exceeds 0.6 µm, so that the powdering resistance and the chipping resistance decrease.
이하 본 발명을 실시예에 의해 상세히 설명한다.Hereinafter, the present invention will be described in detail by way of examples.
<실시예 1><Example 1>
표 1은 유도가열로의 출력비에 따른 플레킹량, 파우더링량, 내치핑성 평가가 개시된 본 발명에 의한 실시 예를 나타낸 것으로 두께 0.8mm인 극저탄소냉간압연 강판을 사용하여 도금부착량을 단면기준으로 60g/m2으로 하였다. 고주파 유도가열로의 하부 존 및 상부 존의 출력비를 달리 하여 가열한 후, 500℃에서 15초 유지하고 에어 미스트를 사용하여 냉각속도를 40℃/초로 하여 제조한 합금화 용융아연 도금강판을 대상으로 플레킹량, 파우더링량, 내치핑성을 평가하여 나타내었다. 플레킹량은 유-비드 시험기(U-bead tester)를 이용하여 전단응력에 의한 도금층의 탈락량을 측정하였으며, 파우더링량은 컵성형시험기(Cupping tester)를 이용하여 압축응력에 의한 도금층의 탈락량을 측정하여 평가하였다. 내치핑성은 전착도장후 -20℃에서 50g의 자갈을 3kgf/cm2의 압력으로 충돌시켜 도금층이 박리되는 면적을 측정하였다.Table 1 shows an embodiment according to the present invention disclosed in the evaluation of the flaking amount, powdering amount, chipping resistance according to the output ratio of the induction furnace furnace 60g based on the plated amount by using the ultra-low carbon cold-rolled steel sheet having a thickness of 0.8mm It was / m2. After heating with different output ratios of the lower zone and the upper zone of the high-frequency induction furnace, the substrate is maintained for 15 seconds at 500 ° C and the cooling rate is 40 ° C / sec using an air mist. The amount of king, amount of powdering and chipping resistance were evaluated and shown. The amount of flaking was measured using the U-bead tester to measure the amount of dropping of the plated layer by the shear stress, and the amount of powdering was measured by the cup forming tester to determine the amount of falling of the plated layer by the compressive stress. Measured and evaluated. The chipping resistance was measured by impacting 50 g of gravel at a pressure of 3 kgf / cm 2 at -20 ° C after electrodeposition coating to measure the area where the plating layer was peeled off.
표 1에서 보듯이 본 발명의 조건을 만족하는 발명예(1-2)는 제타상 및 감마상의 성장이 억제되어 도금층의 플레킹량(합격<10mg), 파우더링량(합격<10mg) 및 내치핑성이(합격<0.5mm2/cm2) 우수하였다. 그러나 유도가열로의 하부/상부 존의 출력비가 2:1 미만인 경우(비교예 1, 비교예2), 합금상중 제타상 분율이 높아 파우더링량 및 치핑성은 감소하나 마찰계수가 증가에 따른 플레킹량이 증가하여, 프레스 성형성 연속작업성이 크게 저하되었다. 또한 하부/상부 존의 출력비가 4:1를 초과한 경우(비교예 3), 취약한 감마상의 두께가 증가하여 파우더링량이 증가하고 내치핑성도 크게 열화되었다.As shown in Table 1, Inventive Example (1-2) that satisfies the conditions of the present invention, the growth of the zeta phase and the gamma phase is suppressed, so that the amount of flaking of the plating layer (pass <10 mg), the amount of powdering (pass <10 mg) and chipping resistance This (pass <0.5 mm <2> / cm <2>) was excellent. However, when the output ratio of the lower / upper zone of the induction furnace is less than 2: 1 (Comparative Example 1, Comparative Example 2), the amount of zeta phase in the alloy phase is high, so that the amount of powdering and chipping is reduced, but the amount of flaking due to the increase of the friction coefficient. Increasingly, press formability continuous workability was greatly reduced. In addition, when the output ratio of the lower / upper zone exceeded 4: 1 (Comparative Example 3), the thickness of the vulnerable gamma phase was increased to increase the amount of powdering and greatly deteriorate chipping resistance.
<실시예 2><Example 2>
표 2는 합금화 처리후 냉각속도에 따른 플레킹량, 파우더링량 및 내치핑성분이 개시된 본 발명에 의한 실시 예를 나타낸 것으로 두께 0.8mm인 극저탄소냉간압연 강판을 사용하여 도금부착량을 단면기준으로 60g/m2으로 하였다. 고주파 유도가열로의 하부 존 및 상부 존의 출력비를 2:1로 하고, 500℃에서 15초 유지한 후 에어 미스트를 사용하여 냉각속도를 달리 하여 제조한 합금화 용융아연 도금강판을 대상으로 플레킹량, 파우더링량, 내치핑성을 평가하여 나타내었다.Table 2 shows the embodiment according to the present invention disclosed the flaking amount, powdering amount and chipping resistance according to the cooling rate after the alloying treatment, using the ultra-low carbon cold rolled steel plate having a thickness of 0.8mm 60g / m2 was set. The output ratio of the lower zone and the upper zone of the high frequency induction furnace is 2: 1, and the amount of flaking is applied to the alloyed hot-dip galvanized steel sheet manufactured by maintaining the cooling rate at 500 ° C. for 15 seconds and varying the cooling rate using an air mist. Powdering amount and chipping resistance were evaluated and shown.
상기 표 2에서 알 수 있는 바와 같이 본 발명의 조건을 만족하도록 합금화 냉각속도를 조절한 발명예 1 및 발명예 2는 적정한 합금화도 및 감마상 두께가 0.5㎛이하로서 내플래킹성, 내파우더링성 및 내치핑성이 매우 우수하였다. 그러나 냉각속도가 30℃/초 미만하면(비교예 1, 비교예 2), 냉각과정중에 합금화가 더 진행되어 감마상이 성장하기 때문에 파우더링량 및 치핑면적이 크게 증가하였다. 반면 냉각속도가 50℃/초를 초과(비교예 3)하여도 파우더링양 및 치핑면적의 감소가 미미하였는데, 이는 본 발명의 30℃∼50/초 냉각속도에서는 더 이상의 합금화가 진행되지 않을만큼 충분한 냉각이 가능하기 때문으로 추정된다. 또한 50/초를 초과한 냉각속도를 확보하기 위해서는 냉각수량을 더욱 증가시키거나, 냉각매체를 기존의 상온상태의 질소에서 액체질소로 변경하여야 하므로 경제적인 측면에서도 바람직하지 못하다.As can be seen in Table 2, Inventive Example 1 and Inventive Example 2, in which the alloying cooling rate was adjusted to satisfy the conditions of the present invention, an appropriate degree of alloying and a gamma phase thickness of 0.5 μm or less, flaking resistance, powdering resistance, and The chipping resistance was very good. However, if the cooling rate is less than 30 ° C / sec (Comparative Example 1, Comparative Example 2), because the alloying proceeds further during the cooling process to increase the gamma phase, the amount of powdering and chipping area increased significantly. On the other hand, even though the cooling rate exceeded 50 ° C / sec (Comparative Example 3), the amount of powdering and chipping area was insignificant, which is sufficient to prevent further alloying at 30 ° C to 50 / sec cooling rate of the present invention. It is assumed that cooling is possible. In addition, in order to secure a cooling rate of more than 50 / sec, the amount of cooling water must be further increased, or the cooling medium must be changed from the existing nitrogen at room temperature to liquid nitrogen.
상술한 바와 같이 본 발명은 별도의 후처리없이 유도가열로의 출력비 조절 및 합금화처리후 냉각속도를 30℃∼50/초로 조절할 경우 합금화 용융아연 도금강판의 가공성 및 내치핑성을 크게 향상시킬 수 있으므로 산업상 이용효과가 매우 크다.As described above, the present invention can greatly improve the workability and chipping resistance of the alloyed hot-dip galvanized steel sheet when the output ratio of the induction furnace is controlled and the cooling rate after the alloying treatment is adjusted to 30 ° C. to 50 / sec. The industrial use effect is very big.
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JPH09184056A (en) * | 1996-01-08 | 1997-07-15 | Nkk Corp | Method for preventing vibration of galvanizing steel strip |
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KR940014876A (en) * | 1992-12-30 | 1994-07-19 | 박득표 | Manufacturing method of alloyed hot-dip zinc hot rolled steel sheet with excellent powder resistance |
JPH07138725A (en) * | 1993-11-18 | 1995-05-30 | Nippon Steel Corp | Induction heating device for galvannealing galvanized steel plate |
JPH09184056A (en) * | 1996-01-08 | 1997-07-15 | Nkk Corp | Method for preventing vibration of galvanizing steel strip |
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KR100928805B1 (en) * | 2002-12-27 | 2009-11-25 | 주식회사 포스코 | Manufacturing method of alloyed hot-dip galvanized steel sheet with beautiful surface |
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