KR100516459B1 - A method for manufacturing soft cold rolled steel sheet by hot direct rolling method - Google Patents
A method for manufacturing soft cold rolled steel sheet by hot direct rolling method Download PDFInfo
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- KR100516459B1 KR100516459B1 KR10-2000-0064151A KR20000064151A KR100516459B1 KR 100516459 B1 KR100516459 B1 KR 100516459B1 KR 20000064151 A KR20000064151 A KR 20000064151A KR 100516459 B1 KR100516459 B1 KR 100516459B1
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- 238000005096 rolling process Methods 0.000 title claims abstract description 91
- 238000000034 method Methods 0.000 title claims abstract description 26
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 21
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims abstract description 16
- 238000005098 hot rolling Methods 0.000 claims abstract description 15
- 238000000137 annealing Methods 0.000 claims abstract description 10
- 238000009826 distribution Methods 0.000 claims abstract description 7
- 238000005097 cold rolling Methods 0.000 claims abstract description 5
- 238000009749 continuous casting Methods 0.000 claims abstract description 4
- 238000005554 pickling Methods 0.000 claims abstract description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- 238000012545 processing Methods 0.000 abstract description 4
- 229910000831 Steel Inorganic materials 0.000 description 13
- 239000010959 steel Substances 0.000 description 13
- 239000002244 precipitate Substances 0.000 description 12
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 239000000463 material Substances 0.000 description 6
- 229910052757 nitrogen Inorganic materials 0.000 description 5
- 238000003303 reheating Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 239000012467 final product Substances 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 238000005297 material degradation process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 230000009466 transformation Effects 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
- B21B1/24—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 in a continuous or semi-continuous process
- B21B1/28—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 in a continuous or semi-continuous process by cold-rolling, e.g. Steckel cold mill
-
- 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
- B21B1/46—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 metal immediately subsequent to continuous casting
- B21B1/463—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 metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2265/00—Forming parameters
- B21B2265/14—Reduction rate
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2265/00—Forming parameters
- B21B2265/22—Pass schedule
Abstract
본 발명은 주로 자동차 내,외판용으로 사용되는 심가공용 연질냉연강판의 제조방법에 관한 것으로서, 극저탄소강을 소재로 하고 열간직송압연법에 의한 연질냉연강판의 제조방법 있어서, 가공성을 향상시키기 위한 수단으로 열간압연스케쥴을 이용해 조압연과 마무리압연의 압하비를 제어함으로써, 우수한 심가공성을 제공할 수 있는 연질냉연강판의 제조방법을 제공하고자 하는데, 그 목적이 있다.The present invention relates to a method for manufacturing a soft cold rolled steel sheet for deep processing mainly used for automotive and exterior panels, in the manufacturing method of a soft cold rolled steel sheet made of ultra low carbon steel by hot direct rolling method, to improve workability It is an object of the present invention to provide a method for manufacturing a flexible cold rolled steel sheet which can provide excellent deep workability by controlling the rolling reduction ratio of rough rolling and finish rolling using a hot rolling schedule as a means.
상기 목적을 달성하기 위한 본 발명은, 극저탄소강을 연속주조한 후, 이어서 조압연 및 마무리압연하고, 산세 및 냉간압연후 연속소둔하는 열간직송압연법에 의한 연질냉연강판의 제조방법에 있어서,In the present invention for achieving the above object, in the method of manufacturing a soft cold rolled steel sheet by hot direct rolling method after continuous casting of ultra low carbon steel, followed by rough rolling and finish rolling, followed by continuous annealing after pickling and cold rolling,
상기 마무리압연은 890℃이하의 페라이트역에서 실시하고, 상기 조압연 및 마무리압연시 압하 배분비(조압연의 압하율/마무리압연의 압하율)가 1.0(50%:50%)~3.5(78%:22%)가 되도록 열간압연스케줄을 조절하는 것을 특징으로 하는 열간직송압연법에 의한 연질냉연강판의 제조방법을 기술적 요지로 한다.The finish rolling is carried out in a ferritic zone of 890 ° C. or less, and the rolling ratio distribution (rolling rate of rough rolling / rolling rate of finish rolling) in the rough rolling and finish rolling is 1.0 (50%: 50%) to 3.5 (78). %: 22%) to produce a soft cold rolled steel sheet by hot direct rolling method characterized in that the hot rolling schedule is adjusted to the technical gist.
Description
본 발명은 주로 자동차 내,외판용으로 사용되는 심가공용 연질냉연강판의 제조방법에 관한 것으로서, 보다 상세하게는 극저탄소강을 소재로 하고 열간직송압연법을 이용한 연질냉연강판의 제조시 열간압연스케쥴을 적절히 조절함으로써, 우수한 심가공성을 갖는 연질냉연강판을 경제적으로 제조하는 방법에 관한 것이다.The present invention relates to a method for manufacturing a soft cold rolled steel sheet for deep processing mainly used for automotive and exterior panels, and more particularly, hot rolling schedule for manufacturing soft cold rolled steel sheet using hot direct rolling method. By adjusting appropriately, the present invention relates to a method for economically manufacturing a soft cold rolled steel sheet having excellent deep workability.
통상 극저탄소강을 소재로 한 심가공용 냉연강판은, 연속주조공정에서 주조된 슬라브를 재가열로에서 고온으로 가열한 후, Ar3변태점 위인 오스테나이트 단상역에서 마무리압연을 완료하여 제조된다. 상기 제조공정에 있어서 열간압연시 압연스케줄은, 다른 일반 강종들과 마찬가지로, 최종적으로 원하는 칫수의 강판을 만들기 위한 수단으로만 이용되어 왔으며, 재질제어를 위해 이용한다는 개념은 전무하였다.The cold rolled steel sheet for deep processing, which is usually made of ultra-low carbon steel, is manufactured by heating a slab cast in a continuous casting process at a high temperature in a reheating furnace and finishing finishing rolling in an austenitic single-phase station above an Ar 3 transformation point. In the manufacturing process, the rolling schedule during hot rolling, like other general steels, has been used only as a means for making a steel plate of the desired size at last, and there is no concept of using it for material control.
한편, 1980년대 중반 이후에는, 극저탄소강의 제조시 페라이트역에서 압연을 실시하면 오히려 압연하중이 작다는 이점을 이용한, 페라이트역 압연에 대한 연구(관련문헌: 철과강85-S1362, 85-S1366, 86-S1343, CAMP-ISIJ vol.2 p.817, 철과강 vol.75 p.782등)가 활발이 진행되었다. 그러나, 상기한 바에 의하면, 양호한 프레스 가공성을 확보하기 위해서, 페라이트역 압연시 윤활압연이 필수적이기 때문에, 실용화가 거의 진행되지 못했다. On the other hand, after the mid-1980s, a study on the ferritic reverse rolling, using the advantage that the rolling load is smaller when rolling in the ferritic station during the production of ultra-low carbon steel (related documents: Iron and steel 85-S1362, 85-S1366 , 86-S1343, CAMP-ISIJ vol.2 p.817, iron and steel vol.75 p.782, etc.). However, according to the above, in order to ensure good press formability, since lubrication rolling is essential at the time of ferritic reverse rolling, practical use has hardly advanced.
한편, 극저탄소강의 페라이트역 압연시, 기존의 재가열로 공정을 거치지 않고, 고온의 슬라브연주후 곧바로 열간압연공정에 투입하는 열간직송압연(HDR, Hot Direct Rolling) 공정은, 무윤활 페라이트역 압연으로도 가공용 연속소둔 연질냉연강판의 제조가 가능한 기술로서, 이미 대한민국 특허출원 제93-31645호, 제94-11394호로 출원된 바 있다. 하지만, 실제 열연공장에서 상기 기술들을 이용해 연질냉연강판을 제조하는 경우에는, 종래의 방법, 즉 재가열로를 거친 후 오스테나이트 단상역에서 마무리압연을 실시하는 방법으로 제조된 제품에 비해, 심가공성의 척도인 r값(소성변형값)(Lankford value)이 다소 저하하기 때문에, 심가공성이 크게 요구되는 난성형성 부품용 제품의 제조에는 적용이 어려운 문제점이 있다. On the other hand, in the case of ferritic reverse rolling of ultra low carbon steel, the hot direct rolling (HDR) process, which is directly put into the hot rolling process after high temperature slab casting without undergoing a conventional reheating process, is a non-lubricated ferritic reverse rolling. As a technology capable of manufacturing continuous annealing soft cold rolled steel sheets for drawing processing, it has already been filed with Korean Patent Application Nos. 93-31645 and 94-11394. However, in the case of manufacturing a flexible cold rolled steel sheet using the above techniques in an actual hot rolling mill, compared to a product manufactured by a conventional method, that is, a finish rolling in an austenitic single-phase station after reheating, Since the r value (the plastic deformation value) (Lankford value), which is a measure, decreases somewhat, there is a problem that it is difficult to apply to the manufacture of a product for a hard-forming component which requires deep workability.
이에, 본 발명자는 상기와 같은 문제점을 해결하기 위하여 연구와 실험을 거듭하고 그 결과에 근거하여 본 발명을 제안하게 된 것으로, 본 발명은 극저탄소강을 소재로 하고 열간직송압연법에 의한 연질냉연강판의 제조방법에 있어서, 가공성을 향상시키기 위한 수단으로 열간압연스케쥴을 이용해 조압연과 마무리압연의 압하비를 제어함으로써, 우수한 심가공성을 제공할 수 있는 연질냉연강판의 제조방법을 제공하고자 하는데, 그 목적이 있다.Accordingly, the present inventors have repeatedly conducted research and experiments to solve the above problems, and propose the present invention based on the results. The present invention is made of ultra-low carbon steel and soft cold rolling by hot direct rolling method. In the manufacturing method of the steel sheet, by using a hot rolling schedule to control the reduction ratio of rough rolling and finish rolling as a means for improving the workability, to provide a method for manufacturing a soft cold rolled steel sheet that can provide excellent deep workability, The purpose is.
상기 목적을 달성하기 위한 본 발명은, 극저탄소강을 연속주조한 후, 이어서 조압연 및 마무리압연하고, 산세 및 냉간압연후 연속소둔하는 열간직송압연법에 의한 연질냉연강판의 제조방법에 있어서,In the present invention for achieving the above object, in the method of manufacturing a soft cold rolled steel sheet by hot direct rolling method after continuous casting of ultra low carbon steel, followed by rough rolling and finish rolling, followed by continuous annealing after pickling and cold rolling,
상기 마무리압연은 890℃이하의 페라이트역에서 실시하고, 상기 조압연 및 마무리압연시 압하 배분비(조압연의 압하율/마무리압연의 압하율)가 1.0(50%:50%)~3.5(78%:22%)가 되도록 열간압연스케줄을 조절하는 것을 특징으로 하는 열간직송압연법에 의한 연질냉연강판의 제조방법에 관한 것이다.The finish rolling is carried out in a ferritic zone of 890 ° C. or less, and the rolling ratio distribution (rolling rate of rough rolling / rolling rate of finish rolling) in the rough rolling and finish rolling is 1.0 (50%: 50%) to 3.5 (78). %: 22%) to a method for manufacturing a soft cold rolled steel sheet by the hot direct rolling method characterized in that the hot rolling schedule is adjusted to be.
이하, 본 발명에 대하여 상세히 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail.
본 발명은 극저탄소강을 소재로 하여 열간직송압연법에 의해 연질의 냉연강판을 제조하는 방법에 관한 것으로서, 본 발명에서 적용되는 소재로는 열간직송 압연법에 의해 연질의 냉연강판으로 제조될 수 있는 통상의 극저탄소강이면 어느 것이나 가능하며, 보다 바람직하게는 강중 탄소의 함량이 100ppm이하이고 Ti 및 Nb이 단독 또는 복합으로 0.005~0.08중량% 함유되어 있는 것이다. 상기 C는, 침입형 고용원소로 작용하여 냉연 및 소둔시 강판의 집합조직 형성과정에서 가공성에 유리한 {111} 집합조직의 형성을 저해할 뿐 만 아니라, 열연 마무리압연시에도 고용원소가 많이 존재하면 가공성에 좋지 않다고 알려진 {100} 및 {110}집합조직이 열연판에 강하게 형성되어 그 영향이 소둔후 까지도 잔존하므로, 그 양을 100ppm이하로 한정하는 것이 바람직하다. 또한, 냉연강판의 가공성에 결정적인 역할을 하는 Ti 및 Nb의 함량은, 이들 원소들이 강중에서 결합하는 불순물 원소인 황(일반적인 극저탄소강에서의 황 함유량은 120ppm이하), 질소(일반적인 극저탄소강에서의 질소 함유량은 60ppm이하) 및 탄소함량을 고려하여 설정하는데, 이들 성분과 모두 결합하여 TiN, TiS, Ti4C2S2, TiC, NbN, NbC, TiNbC등의 석출물을 형성하고도 잉여로 남을 수 있도록, 단독 또는 복합으로 0.005~0.08중량% 첨가하는 것이 바람직하다. 만일, 상기 Ti 및 Nb의 함량이 단독 또는 복합으로 0.005% 미만이어서, 상기의 황, 질소 및 탄소 등의 고용원소가 강중에 잔존하는 경우에는, 가공성이 나빠지고, 소둔재결정온도가 높아질 뿐 만 아니라, 시효에 의한 재질열화의 원인이 된다. 또한, 그 함량이 0.08% 이상이면, 오히려 재결정온도를 상승시키고 매우 비경제적이기 때문에, 바람직하지 않다.The present invention relates to a method for producing a soft cold rolled steel sheet by hot direct rolling method using ultra low carbon steel as a material, the material applied in the present invention can be produced as a soft cold rolled steel sheet by a hot direct rolling method Any conventional ultra low carbon steel can be used, and more preferably, the content of carbon in the steel is 100 ppm or less and Ti and Nb are contained 0.005 to 0.08% by weight alone or in combination. The C acts as an invasive solid solution and inhibits formation of {111} texture, which is advantageous for processability, during formation of the texture of the steel sheet during cold rolling and annealing. Since {100} and {110} aggregates, which are known to be poor in workability, are strongly formed in the hot rolled sheet and the influence remains even after annealing, the amount thereof is preferably limited to 100 ppm or less. In addition, the contents of Ti and Nb, which play a decisive role in the workability of cold rolled steel sheets, include sulfur, which is an impurity element to which these elements bind in steel (120 ppm or less in general ultra low carbon steel), and nitrogen (in general ultra low carbon steel). The nitrogen content of is set to 60ppm or less) and the carbon content, which is combined with all of these components to form a precipitate such as TiN, TiS, Ti 4 C 2 S 2 , TiC, NbN, NbC, TiNbC and remain as excess. In order to be able to, it is preferable to add 0.005 to 0.08% by weight alone or in combination. If the content of Ti and Nb alone or in combination is less than 0.005%, the solid solution such as sulfur, nitrogen and carbon remain in the steel, resulting in poor workability and high annealing material crystal temperature. This may cause material degradation due to aging. Further, if the content is 0.08% or more, it is not preferable because it raises the recrystallization temperature and is very uneconomical.
이와 같이 조성된 극저탄소강을 슬라브로 연속주조한 후 고온의 재가열없이, 직접 열간압연할 때, 조압연과 마무리압연의 압하배분비를 1.0(50%:50%)~3.5(78%:22%)로 설정하는 것이 바람직한데, 그 이유는 다음과 같다.When continuously casting ultra-low carbon steel thus formed into slabs and directly hot rolling without high temperature reheating, the rolling ratio of rough rolling and finish rolling is 1.0 (50%: 50%) to 3.5 (78%: 22 %) Is preferable because of the following reasons.
본 발명의 강중에 첨가된 Ti, Nb등은 질소,황,탄소와 같은 강중 불순물 고용원소와 결합하여 석출물을 형성하는데, 이들 석출물들의 크기 및 분포상태는 최종 냉연제품의 가공성에 크게 영향을 미친다. 즉, 열연판 중 C,N,S 등의 불순물원소가 전부 석출물로 고정된 상태에서, 석출물의 크기가 수십Å 이하인 극미세 석출물은 거의 존재하지 않고 주로 수백Å 이상의 크기로 균일하게 분포하는 경우에는, 최종제품인 냉연강판의 r값이 크게 개선되는 것이다. 한편, 이들 석출물이 활발하게 석출되는 온도대는 주로 열간압연시의 온도영역과 일치하기 때문에 결국 극저탄소강중 석출물의 크기 및 분포상태는 열간압연온도 및 압하량 등에 의해 크게 좌우되는 것이다. 따라서, 압연시 이러한 석출물들의 석출을 촉진시킬 수 있는 온도영역에서 압하량을 크게 하는 것이 중요하다. 특히, 종래 압연방식에 비해 석출의 지연이 큰, 극저탄소강을 열간직송압연에 의해 압연하는 경우에는, 더욱더 마무리압연의 압하량을 높일수록, 석출물의 형성이 용이해지고, 그 크기도 수백Å 이상이 주종을 이루도록 된다. Ti, Nb, and the like added to the steel of the present invention combines with solid impurities such as nitrogen, sulfur, and carbon to form precipitates. The size and distribution of these precipitates greatly affect the processability of the final cold rolled product. That is, in the state where all impurity elements such as C, N, S, etc. in the hot rolled sheet are fixed as precipitates, very fine precipitates having a precipitate size of several tens of micrometers or less are hardly present and are distributed uniformly in the size of several hundred micrometers or more. As a result, the r value of the cold rolled steel sheet as a final product is greatly improved. On the other hand, since the temperature zone where these precipitates are actively precipitated coincides mainly with the temperature range during hot rolling, the size and distribution of precipitates in the ultra low carbon steel are largely dependent on the hot rolling temperature and the amount of rolling. Therefore, it is important to increase the amount of reduction in the temperature range that can promote the precipitation of these precipitates during rolling. In particular, when rolling ultra low carbon steel, which has a greater delay in precipitation than conventional rolling methods, by hot direct rolling, the higher the reduction amount of finish rolling is, the easier it is to form precipitates, and the size is more than several hundred microseconds. This predominance will be achieved.
즉, 본 발명에서와 같이, 마무리압연의 압하량을 높여서 조압연과 마무리압연의 압하배분비를 1.0(50%:50%)~3.5(78%:22%)로 설정한 이유는, 열연판중에 고용원소는 존재하지 않으면서도 크기가 수백Å 이상인 석출물이 주로 분포하도록 조정함으로써, 최종제품의 r값을 높이기 위함이다. 또한, 상기 압하배분비가 1.0미만으로 마무리압연의 압하량이 너무 커지면, 압연부하가 크게 증대하고, 또한 3.5 이상에서는 r값의 상승효과가 거의 나타나지 않기 때문에 바람직하지 않다.That is, as in the present invention, the reduction ratio of the rough rolling and the finish rolling was set to 1.0 (50%: 50%) to 3.5 (78%: 22%) by increasing the amount of reduction in finish rolling. This is to increase the r value of the final product by adjusting the distribution of precipitates of hundreds of microns or more without the presence of employment elements. In addition, when the reduction ratio of the finish rolling is too large and the rolling reduction ratio is less than 1.0, the rolling load is greatly increased, and since the synergistic effect of the r value hardly appears at 3.5 or more, it is not preferable.
한편, 상기 열간압연시 마무리압연은 890℃ 이하의 페라이트 단상역에서 마무리하는 것이 바람직하다. 그 이유는, 마무리압연온도가 890℃ 이상이면, 페라이트와 오스테나이트의 2상역에서 압연이 실시되어 최종 제품의 가공성을 크게 해치는 혼립조직을 유발하기 때문이다. On the other hand, the finish rolling during hot rolling is preferably finished in the ferrite single-phase zone of 890 ℃ or less. The reason is that when the finish rolling temperature is 890 ° C or higher, rolling is performed in the two-phase region of ferrite and austenite, causing a mixed structure that greatly impairs the workability of the final product.
상기와 같은 방식으로 압연된 열연강판은, 통상의 방법으로 산세에 의해서 표면 스케일을 제거한 뒤, 50~85%의 압하율로 압연하여 냉연판을 만들고, 720℃이상의 비교적 저온에서 연속소둔한다.The hot rolled steel sheet rolled in the above manner removes the surface scale by pickling in a conventional manner, and then rolls it at a reduction ratio of 50 to 85% to form a cold rolled sheet, which is continuously annealed at a relatively low temperature of 720 ° C or higher.
이와 같이 하여 제조된 연질의 냉연강판은, 열연시 무윤활 페라이트역 압연으로도, 우수한 심가공성을 확보할 수 있다. The soft cold rolled steel sheet produced in this way can ensure excellent deep workability even by the non-lubricated ferrite reverse rolling during hot rolling.
이하, 실시예를 통하여 본 발명을 보다 상세히 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.
(실시예)(Example)
하기 표1과 같은 성분조성을 갖는 슬라브를 소재로 하여, 하기 표2의 열간압연 조건으로 열연판을 제조하였다. 그 다음, 상기에서 얻어진 열연판을 산세하여 75%의 압하율로 냉간압연한 후 연속소둔을 실시한 다음, 이 냉연판에 대한 기계적성질을 측정하고, 그 결과를 하기 표3에 나타내었다. A hot rolled sheet was manufactured under the hot rolling conditions of Table 2, using the slabs having a composition as shown in Table 1 below. Then, the hot rolled sheet obtained above was pickled and cold rolled at a reduction ratio of 75%, followed by continuous annealing, and then the mechanical properties of the cold rolled sheet were measured, and the results are shown in Table 3 below.
삭제delete
상기한 바와 같이 본 발명에 의하면, 강중 석출물의 금속학적 거동을 적극적으로 이용하는 압연방식을 실시함으로써, 생산성 향상, 제조기간 단축, 소둔로내 스트립 통판성 개선 및 에너지절감등의 효과를 얻으면서도 심가공성이 우수한 연질냉연강판의 제조가 가능할 뿐 만 아니라, 최종 마무리압연의 압하율 상향에 의한 부가적인 생산성 향상을 꾀할 수 있는 것이다.As described above, according to the present invention, by implementing a rolling method that actively uses the metallurgical behavior of the precipitates in the steel, while improving the productivity, shortening the manufacturing period, improve the strip sheet in the annealing furnace, energy saving, etc. Not only is it possible to manufacture the excellent soft cold rolled steel sheet, but it is also possible to further improve productivity by increasing the reduction ratio of the final finish rolling.
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KR940005821A (en) * | 1992-06-08 | 1994-03-22 | 도사키 시노부 | High strength cold rolled steel with excellent pull-out and manufacturing method |
KR940014846A (en) * | 1992-12-30 | 1994-07-19 | 박득표 | Manufacturing method of cold rolled steel sheet with excellent deep workability |
KR950018534A (en) * | 1993-12-29 | 1995-07-22 | 조말수 | Manufacturing method of ultra low carbon cold rolled steel sheet with excellent workability and age resistance |
JPH10168517A (en) * | 1996-12-13 | 1998-06-23 | Kawasaki Steel Corp | Production of extra low carbon cold rolled steel sheet |
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KR940005821A (en) * | 1992-06-08 | 1994-03-22 | 도사키 시노부 | High strength cold rolled steel with excellent pull-out and manufacturing method |
KR940014846A (en) * | 1992-12-30 | 1994-07-19 | 박득표 | Manufacturing method of cold rolled steel sheet with excellent deep workability |
KR950018534A (en) * | 1993-12-29 | 1995-07-22 | 조말수 | Manufacturing method of ultra low carbon cold rolled steel sheet with excellent workability and age resistance |
JPH10168517A (en) * | 1996-12-13 | 1998-06-23 | Kawasaki Steel Corp | Production of extra low carbon cold rolled steel sheet |
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