KR100402009B1 - A method for manufacturing a hot rolled sheet steel for the both side enamel coating - Google Patents
A method for manufacturing a hot rolled sheet steel for the both side enamel coating Download PDFInfo
- Publication number
- KR100402009B1 KR100402009B1 KR10-1999-0042771A KR19990042771A KR100402009B1 KR 100402009 B1 KR100402009 B1 KR 100402009B1 KR 19990042771 A KR19990042771 A KR 19990042771A KR 100402009 B1 KR100402009 B1 KR 100402009B1
- Authority
- KR
- South Korea
- Prior art keywords
- enamel
- hot rolled
- hot
- steel sheet
- rolled steel
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
본 발명은 법랑용 열연강판의 제조방법에 관한 것으로, C,B,N,Mn 및 S등의 합금원소를 적당히 첨가하고 열연조건을 제어함으로써, 법랑용 열연강판에 요구되는 내피쉬스케일성, 소성후 강도 및 법랑밀착성 등이 우수한 법랑용 열연강판의 제조방법을 제공하고자 하는데, 그 목적이 있다.The present invention relates to a method for manufacturing a hot rolled steel sheet for enamel, by adding alloying elements such as C, B, N, Mn and S appropriately and controlling the hot rolling conditions, the fish scale resistance and plasticity required for the hot rolled steel sheet for enamel It is intended to provide a method for producing an enameled hot rolled steel sheet having excellent strength and enamel adhesion, and the purpose thereof.
상기 목적을 달성하기 위한 본 발명은, 법랑용 열연강판의 제조방법에 있어서,The present invention for achieving the above object, in the manufacturing method of the hot rolled steel sheet for enamel,
중량%로 C:0.1% 이하, Mn:0.1~0.5%, S:0.01~0.05%, P:0.03% 이하, B:0.004~0.015%, N:0.006~0.02%, Al:0.01~0.1%을 함유하고, 0.0005%<N-1.3B을 만족하고, 나머지 Fe 및 기타 불가피한 불순물을 함유하는 강을 1300℃ 이하에서 재가열한 후, 열간압연하되 열간마무리 압연개시온도를 1150℃ 이하로 하고 마무리 압연시 총 압하율을 80% 이상으로 하며, 600℃ 이상의 온도에서 권취하는 것을 특징으로 하는 양면 법랑용 열연강판의 제조방법에 관한 것을 그 기술적 요지로 한다.C: 0.1% or less, Mn: 0.1 to 0.5%, S: 0.01 to 0.05%, P: 0.03% or less, B: 0.004 to 0.015%, N: 0.006 to 0.02%, Al: 0.01 to 0.1% by weight% Steel, which satisfies 0.0005% <N-1.3B, and re-heats the steel containing the remaining Fe and other unavoidable impurities at 1300 ° C. or lower, and then hot-rolls to obtain a hot finish rolling start temperature of 1150 ° C. or lower, and finish rolling The total rolling reduction is 80% or more, and the technical gist of the method for producing a double-sided enameled hot rolled steel sheet, which is wound at a temperature of 600 ° C or higher.
Description
본 발명은 온수탱크, 액체비료탱크, 사일로 및 개스렌지 부품 등에 이용되는 법랑용 열연강판의 제조방법에 관한 것으로, 보다 상세하게는 비교적 높은 강도가 요구되고 소재의 두께가 두꺼워 열연강판을 사용해야 하는 법랑제품의 소재인 법랑용 열연강판의 제조방법에 관한 것이다.The present invention relates to a method for manufacturing an enameled hot rolled steel sheet used in hot water tanks, liquid fertilizer tanks, silos and gas stove parts, more specifically, a relatively high strength is required and the thickness of the material thick enamel enamel should be used The present invention relates to a method for producing enameled hot rolled steel sheet.
일반적으로 법랑용 강판은 법랑처리후 여러가지 법랑결함이 발생되지 않도록 성분이나 공정을 적절히 조정하여 제조한다. 법랑용 강판이 아닌 일반 강판을 사용하여 법랑처리를 하면 결함이 발생하는데, 그중 가장 치명적인 결함은 피쉬스케일 결함이다. 상기 피쉬스케일 결함은 강중 수소의 거동에 관계하는 것으로, 이를 방지하기 위해서는 강중 수소를 저장할 수 있는 장소를 제공해야 한다. 수소를 저장할 수 있는 장소로는 개재물, 석출물 등과 소지철간의 계면 또는 이들이 압연되면서 생성되는 미세한 틈 등을 들 수 있다. 이들 중 미세한 틈은 주로 냉간압연중 생성되는 것으로, 수소를 저장할 수 있는 가장 큰 장소로 알려져 있는데, 고온에서압연할 경우 미세한 틈의 생성이 어렵기 때문에 개재물 또는 석출물에 의해 내피쉬스케일성을 확보해야 한다. 따라서, 열연판의 경우 내피쉬스케일성을 확보하기 위해서는 냉연판에 비해 더 많은 양의 석출물 또는 개재물을 석출시켜야 한다.In general, the steel sheet for enamel is produced by appropriately adjusting the components or processes so that various enamel defects do not occur after enamel processing. Enamel processing is performed using general steel sheet instead of enamel steel sheet, the most fatal one of which is fish scale defect. The fish scale defect is related to the behavior of hydrogen in the river, and to prevent this, it is necessary to provide a place for storing hydrogen in the river. The place where hydrogen can be stored may include an interface between inclusions, precipitates, and the base iron, or a minute gap generated while rolling them. Among these, the micro cracks are mainly generated during cold rolling, and are known as the largest places for storing hydrogen. When rolling at high temperatures, it is difficult to form micro cracks, and thus fish scale resistance must be secured by inclusions or precipitates. do. Therefore, in order to secure fish-scale resistance in the case of hot rolled sheet, a larger amount of precipitates or inclusions must be deposited.
종래의 양면 법랑용 열연강판의 일례로, 일본 특허공보 소58-1170에서 제시한 성분은 C: 0.02~0.1%, Mn:0.05~0.4%, Ti:0.05~0.3%로서, Ti 탄화물을 이용하여 내피쉬스케일성을 확보한 기술이다. 그러나, 상기 방법에서는 첨가되는 Ti의 함량이 높기 때문에, 제조원가가 높고 산화성이 매우 높은 Ti를 다량 첨가함에 따라 Ti 산화물이 턴디쉬 노즐에 부착되어 노즐막힘현상이 발생하기 쉬우며, 이것이 강판 표면결함으로 진전하는 문제가 있다.As an example of a conventional hot rolled steel sheet for double-sided enamel, the components described in Japanese Patent Publication No. 58-1170 are C: 0.02 to 0.1%, Mn: 0.05 to 0.4%, and Ti: 0.05 to 0.3%, using Ti carbide. It is a technology that has secured fish scale resistance. However, in the above method, since the content of Ti added is high, the Ti oxide is attached to the tundish nozzle by the addition of a large amount of Ti having a high manufacturing cost and very oxidizing property, and it is easy to cause nozzle clogging. There is a problem with progress.
이에 본 발명은, 상기한 문제점을 해결하기 위한 것으로, 종래기술에서 문제가 된 Ti를 이용하지 않고 대신 C,B,N,Mn 및 S등의 합금원소를 적당히 첨가하고 열연조건을 제어함으로써, 내피쉬스케일성 및 법랑 밀착성과 강도가 우수한 양면 법랑용 열연강판의 제조방법을 제공하는데, 그 목적이 있다.Accordingly, the present invention is to solve the above problems, and by using alloys such as C, B, N, Mn and S appropriately and controlling hot rolling conditions without using Ti, which is a problem in the prior art, To provide a method for producing a hot rolled steel sheet for double-sided enamel having excellent fish scale and enamel adhesion and strength, the object is to.
상기 목적을 달성하기 위한 본 발명의 양면 법랑용 열연강판의 제조방법은,Method for producing a double-sided enameled hot rolled steel sheet of the present invention for achieving the above object,
중량%로 C:0.1% 이하, Mn:0.1~0.5%, S:0.01~0.05%, P:0.03% 이하, B:0.004~0.015%, N:0.006~0.02%, Al:0.01~0.1%을 함유하고, 0.0005%<N-1.3B을 만족하고, 나머지 Fe 및 기타 불가피한 불순물을 함유하는 강을 1300℃ 이하에서 재가열한 후, 열간압연하되 열간마무리 압연개시온도를 1150℃ 이하로 하고 마무리 압연시 총 압하율을 80% 이상으로 하며, 600℃ 이상의 온도에서 권취하는 것을 특징으로 하는 양면 법랑용 열연강판의 제조방법에 관한 것이다.C: 0.1% or less, Mn: 0.1 to 0.5%, S: 0.01 to 0.05%, P: 0.03% or less, B: 0.004 to 0.015%, N: 0.006 to 0.02%, Al: 0.01 to 0.1% by weight% Steel, which satisfies 0.0005% <N-1.3B, and re-heats the steel containing the remaining Fe and other unavoidable impurities at 1300 ° C. or lower, and then hot-rolls to obtain a hot finish rolling start temperature of 1150 ° C. or lower, and finish rolling The total rolling reduction is 80% or more, and relates to a method for producing a double-sided enameled hot rolled steel sheet, which is wound at a temperature of 600 ° C. or higher.
이하, 본 발명을 상세히 설명한다.Hereinafter, the present invention will be described in detail.
먼저, 상기 성분범위의 한정이유에 대해서 설명한다.First, the reason for limitation of the said component range is demonstrated.
상기 C의 첨가량은 0.1% 이하로 하는 것이 바람직한데, 그 이유는 0.1%보다 많이 첨가될 경우 강판 표면에 시멘타이트의 양이 많아져, 법랑처리시 탄화물의 산화반응으로 인해 비정상적으로 성장하는 기포에 의한 결함발생 확율이 높기 때문이다.The amount of C added is preferably 0.1% or less. The reason for this is that when the amount is more than 0.1%, the amount of cementite increases on the surface of the steel sheet, which is caused by bubbles growing abnormally due to the oxidation of carbides during enameling. This is because the probability of defects is high.
상기 Mn은 통상 강중에 고용된 황을 망간황화물로 석출시켜 고용 황에 의한 적열취성(Hot shortness)을 방지하는 역할을 하는데, 본 발명에서는 망간황화물의 수소흡장능 향상을 적극 활용하기 위해 첨가한다. Mn을 0.1% 미만으로 첨가하면 망간황화물의 양 또는 크기가 적어 내피쉬스케일성 향상효과가 거의 없고, Mn첨가량을 0.5% 이상으로 할 경우, 더이상의 내피쉬스케일성 향상효과가 없을 뿐 아니라 제조원가가 높아지므로, Mn의 첨가량은 0.1~0.5%로 제한하였다.The Mn usually serves to prevent hot shortness caused by solid solution sulfur by precipitating sulfur dissolved in steel as manganese sulfide. In the present invention, Mn is added to take advantage of the improvement of hydrogen absorption ability of manganese sulfide. If the amount of Mn is less than 0.1%, the amount or size of manganese sulfide is little, and there is little effect of improving fish scale resistance. If the amount of Mn added is 0.5% or more, there is no further effect of improving fish scale resistance and manufacturing cost. Since it increased, the amount of Mn added was limited to 0.1 to 0.5%.
상기 S은 일반적으로 강의 물성을 저해하는 원소로 알려져 있으나, 본 발명의 경우 망간황화물로 석출시켜 내피쉬스케일성을 향상시키기 위해 첨가한다. 그 첨가량이 0.01% 미만이면 망간황화물 석출량이 너무 적어 효과가 거의 없고, 0.05% 를 초과하면 연성을 저하시키므로, 황은 0.01~0.05%로 첨가하는 것이 바람직하다.The S is generally known as an element that inhibits the physical properties of the steel, but in the present invention, it is added to precipitate into manganese sulfide to improve fish scale resistance. If the added amount is less than 0.01%, the amount of precipitated manganese sulfide is too small to have little effect. If the amount is more than 0.05%, the ductility is lowered. Therefore, sulfur is preferably added at 0.01 to 0.05%.
상기 P은 0.03% 이상 첨가될 경우 연성이 저하하므로, 상한값을 0.03%로 제한하였다.When P is added at 0.03% or more, ductility decreases, so the upper limit is limited to 0.03%.
상기 B은 질소와 결합해 보론질화물을 생성하여 내피쉬스케일성을 향상시키므로 첨가한다. B첨가량을 0.004% 이상으로 하였을 때, 피쉬스케일 결함이 발생하지 않았기 때문에, 하한값을 0.004%로 하였다. 보론의 첨가량이 많을수록 수소흡장능은 증가하여 내피쉬스케일성은 향상하지만, 적정 이상의 내피쉬스케일성을 확보할 필요는 없으며, 그 양이 지나칠 경우, 성형성이 크게 저하하므로 상한값은 0.015%로 제한하였다.B is added because it combines with nitrogen to form boron nitride to improve fish scale resistance. Since the fish scale defect did not generate | occur | produce when the addition amount B was 0.004% or more, the lower limit was made into 0.004%. As the amount of boron added increases, the hydrogen absorbing ability increases to improve fish scale resistance, but it is not necessary to secure fish scale resistance higher than the appropriate amount. When the amount is excessive, the upper limit is limited to 0.015% because the moldability greatly decreases. .
상기 N는 B과 결합하여 보론질화물로 석출하여 내피쉬스케일성을 확보하기 때문에 첨가한다. 보론첨가량의 최소값인 0.004%를 전부 석출하는데 필요한 이론적 질소량(가령 BN으로 석출)은 0.0052%이지만, 고용상태로 잔존하는 보론을 완전히 석출하기 위해서는 최소한 0.006% 이상의 질소가 필요하므로, 하한값은 0.006%로 하였다. 질소의 첨가량이 증가할수록 석출되는 석출물이 양이 많아 내피쉬스케일성은 향상하지만, 너무 많을 경우 연성을 저하하므로 상한값은 0.02%로 제한하였다.The N is added to bind with B because it precipitates as boron nitride to secure fish scale resistance. The theoretical amount of nitrogen needed to deposit all of the minimum amount of boron added, 0.004% (for example, precipitation as BN) is 0.0052%, but at least 0.006% of nitrogen is required to completely deposit boron remaining in solid solution, so the lower limit is 0.006%. It was. As the amount of nitrogen increases, the amount of precipitates precipitated increases so that the fish scale resistance is improved, but when too much, the ductility decreases, so the upper limit is limited to 0.02%.
상기 Al은 탈산제로, 0.01% 이하에서는 탈산효과가 적고 0.1% 이상에서는 Al 산화물의 증가로 표면결함 발생확율이 높으므로 상한값을 0.1%로 제한하였다.Since Al is a deoxidizer, the deoxidation effect is less at 0.01% or less and the probability of surface defects is increased due to the increase of Al oxide at 0.1% or more, so the upper limit is limited to 0.1%.
상기 B 및 N첨가량을 0.0005%<N-1.3B로 제한한 것은 강중에 고용 보론이 잔존할 경우, 내피쉬스케일성을 향상효율이 낮을 뿐 아니라, 연성이 급격히 저하하므로 N-1.3B의 하한값을 0.0005%로 하였다.The amount of B and N added to 0.0005% <N-1.3B is limited to improve the efficiency of fish scale resistance when the boron remains in the steel, and lower the ductility so that the lower limit of N-1.3B is reduced. It was set as 0.0005%.
다음으로, 열연조건의 한정이유에 대하여 설명한다.Next, the reason for limitation of hot rolling conditions is demonstrated.
상기와 같이 조성되는 강 슬라브를 재가열하여 열간압연 및 권취하는 법랑용 열연강판의 제조방법에 있어서, 상기 재가열온도는 1300℃ 이하로 하는데, 그 이유는 재가열온도가 1300℃보다 높으면 BN석출물이 완전히 용해해 석출물의 크기 및 양이 적어져 내피쉬스케일성이 저하하기 때문이다. 또한, 상기 재가열온도의 하한치는 1200℃ 정도가 바람직하며, 1250℃ 정도가 가장 바람직하다.In the manufacturing method of the enameled hot rolled steel sheet to reheat the steel slab formed as described above and hot rolled and wound, the reheating temperature is 1300 ℃ or less, because the BN precipitate is completely dissolved when the reheating temperature is higher than 1300 ℃ This is because fish scale resistance decreases due to the smaller size and amount of the precipitates. In addition, the lower limit of the reheating temperature is preferably about 1200 ° C, and most preferably about 1250 ° C.
상기 마무리압연 개시온도는 1150℃ 이하로 하는 것이 바람직한데, 1150℃ 보다 높은 온도에서 압연하면 석출물의 양이 적어 수소흡장원으로 작용하는 석출물과 기지금속간의 계면적이 적어 내피쉬스케일성이 저하하기 때문이다. 따라서, 마무리압연 개시온도를 1150℃ 이하로 제한하며, 바람직하게는 1100℃ 정도가 좋다. 또한, 마무리압연의 총 압하율이 80% 이하로 낮을 경우, 석출물과 기지금속간의 계면적이 적어져 내피쉬스케일성이 낮아지므로, 마무리압연 총 압하율은 80% 이상으로 제어하는 것이 바람직하다.It is preferable that the finish rolling start temperature be 1150 ° C. or lower, because rolling at a temperature higher than 1150 ° C. decreases the amount of precipitates and decreases the fish scale resistance due to the small interfacial area between the precipitates serving as a hydrogen storage source and the base metal. to be. Therefore, finish rolling start temperature is limited to 1150 degrees C or less, Preferably about 1100 degreeC is good. In addition, when the total rolling reduction rate of the finish rolling is lower than 80%, since the interface area between the precipitate and the base metal decreases, the fish scale resistance is lowered, the final rolling total reduction rate is preferably controlled to 80% or more.
통상 권취온도가 높으면 석출물의 크기 및 양은 증가하기 때문에 유리한데, 본 발명에서는 상기 권취온도의 하한치를 600℃로 제한하였다. 그 이유는 600℃미만에서 권취할 경우, 내피쉬스케일성이 저하하기 때문이다. 또한, 상기 권취온도는 650℃ 정도가 가장 바람직하며, 상한치는 700℃ 정도이다.In general, the higher the coiling temperature is advantageous because the size and amount of the precipitate increases, the present invention limited the lower limit of the coiling temperature to 600 ℃. The reason for this is that the fish scale resistance is lowered when winding at less than 600 ° C. In addition, the winding temperature is most preferably about 650 ℃, the upper limit is about 700 ℃.
이하, 실시예를 통해 본 발명을 보다 상세히 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.
(실시예)(Example)
하기 표1과 같은 조성의 강을 슬라브로 제조하고, 1250℃가열로에서 1시간 유지한 후 열간압연을 실시하였다. 이 때 열간마무리 압연개시온도는 1100℃, 권취온도는 650℃로 하였으며, 총 마무리 압하율을 89%로 하여 최종두께를 3.2mm로 하였다. 또한, 열간압연 조건변화에 따른 재질 및 법랑특성변화를 조사하기 위해 마무리압연 개시온도를 1200℃, 마무리압연시 총 압하율을 75% 및 권취온도를 550℃로 변화시켰다. 그 다음, 상기 열간압연된 시편을 산세처리하여 표면의 산화피막을 제거하한 후, 법랑특성 및 기계적 특성을 조사하기 위한 법랑처리시편을 70mm×150mm의 크기로 각각 절단하였으며, 인장시편은 ASTM규격(ASTM E-8 standard)에 의한 표준시편으로 가공하였다.Steel having a composition as shown in Table 1 below was manufactured as a slab, and maintained at 1250 ° C. for 1 hour, followed by hot rolling. At this time, the hot finish rolling start temperature was 1100 ° C., the coiling temperature was 650 ° C., and the final thickness was 3.2% with a total finishing reduction of 89%. In addition, in order to investigate the change of material and enamel characteristics according to the change of hot rolling condition, the finish rolling start temperature was 1200 ℃, the total rolling rate was 75% and the winding temperature was changed to 550 ℃. Then, the hot-rolled specimen was pickled to remove the oxide film on the surface, and the enamel treated specimens were then cut into 70 mm × 150 mm sizes to examine the enamel and mechanical properties, and the tensile specimen was ASTM standard. It was processed into a standard specimen according to ASTM E-8 standard).
상기와 같이 제조된 인장시편에 대하여 인장시험기(INSTRON사, Model 6025)를 이용해 항복강도, 인장강도 및 연신율을 측정하고, 그 결과를 하기 표2에 나타내었다. 그리고, 법랑처리용 시편에 대해서는 70℃, 10% 황산용액에서 5분간 침적하는 산처리를 실시하고, 온수로 세척한 후 80℃로 유지한 7% 황산니켈용액에 5분간 침적하는 니켈처리를 하였다. 니켈처리가 끝난 시편은 온수로 세척한 후, 85℃로 유지한 3.6g/l탄산소다+1.2g/l붕사수용액에 5분간 침적하는 중화처리하였다. 다음, 전처리가 완료된 시편에 하유유약(Ground Coat)을 도포한 후 200℃에서 10분간 건조하여 수분을 완전히 제거하였다. 건조가 끝난 시편은 830℃에서 7분간 유지하고 노점온도 30℃의 분위기에서 소성처리를 실시한 후 공냉하는 법랑처리를 하였다. 그 다음, 피쉬스케일 결함수는 육안으로 조사하고, 밀착성은 200g 강구를 1M 높이에서 낙하하여 탈락된 법랑층을 육안으로 관찰하여, 그 평가결과를 하기 표2에 나타내었다.Yield strength, tensile strength and elongation were measured using a tensile tester (INSTRON, Model 6025) on the tensile specimens prepared as described above, and the results are shown in Table 2 below. The enameled specimens were subjected to acid treatment for 5 minutes in 70 ° C. and 10% sulfuric acid solution, and then washed with hot water and nickel treated for 5 minutes in 7% nickel sulfate solution maintained at 80 ° C. . The nickel-treated specimens were washed with warm water and neutralized by immersion in 3.6 g / l sodium carbonate + 1.2 g / l borax solution maintained at 85 ° C for 5 minutes. Next, after the pretreatment was completed, the coating was applied to the ground glaze (Ground Coat) and dried at 200 ° C. for 10 minutes to completely remove moisture. The dried specimens were kept at 830 ° C. for 7 minutes and subjected to firing in an atmosphere of dew point temperature of 30 ° C., followed by enameling of air cooling. Then, the number of fish scale defects were visually inspected, and the adhesion was visually observed by dropping the 200 g steel ball at 1M height and visually dropping the enamel layer, and the evaluation results are shown in Table 2 below.
상기 표1 및 2에 나타낸 바와 같이 본 발명의 범위에 속하는 발명강(1)~(4)는 가혹한 조건에서도 피쉬스케일이 발생하지 않았고, 소성후 항복강도도 25kgf/㎟ 이상이 되어 법랑처리용 열연판으로 적당하였다. 반면, 비교강(1)은 보론의 함량이 본 발명의 범위보다 낮아 33개의 피쉬스케일결함이 발생하였다. 비교강(2)는 보론 함량은 본 발명 범위에 속하나 질소함량이 0.0038%로 본 발명의 범위에서 벗어났을 뿐 아니라, N-1.3B값도 -0.0118로 음의 값을 가졌기 때문에, 46개의 피쉬스케일결함이 발생하였다. 비교강(3)은 성분은 본 발명범위에 속하나 열연조건중 압연개시온도가 높고, 권취온도도 낮으며 총 압하율 또한 75%로 매우 낮아 25개의 피쉬스케일결함이 발생하였다. 한편, 비교강(4)는 탄소함량이 너무 높아 법랑처리시 기포결함이 발생하여 법랑용으로 사용할 수가 없다.As shown in Tables 1 and 2, the invention steels (1) to (4) belonging to the scope of the present invention did not generate fish scale even under severe conditions, and the yield strength after firing became 25 kgf / mm 2 or more, so that the hot rolled enamel was treated. It was suitable as a plate. On the other hand, the comparative steel (1), the content of boron is lower than the range of the present invention 33 fish scale defects occurred. Comparative steel (2) is 46 fish scale because boron content is within the scope of the present invention, but the nitrogen content is 0.0038%, not only out of the scope of the present invention, but also the N-1.3B value is negative value of -0.0118. A defect occurred. Comparative steel (3) is a component within the scope of the present invention, but the hot rolling start temperature of the hot rolling conditions, the winding temperature is low, the total reduction rate is also very low as 75% occurred 25 fish scale defects. On the other hand, the comparative steel (4) is too high in the carbon content bubble defects during the enamel processing can not be used for enamel.
상술한 바와 같이 본 발명으로 제조된 법랑용 열연강판은, 내피쉬스케일성이 우수하여 법랑제품의 치명적인 결함인 피쉬스케일(Fishscale)결함이 전혀 발생하지않고 법랑 밀착성 및 소성후 강도가 모두 우수하기 때문에, 특히 소재의 두께가 두꺼워야 하고, 양면에 법랑처리를 해야 하는 제품에 적용할 수 있다.As described above, the enameled hot rolled steel sheet produced by the present invention has excellent fish scale resistance, so that no fish scale defects, which are fatal defects of enamel products, are generated at all, and both enamel adhesion and post-calcination strength are excellent. In particular, it can be applied to products that need to be thick and have enamel processing on both sides.
Claims (1)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR10-1999-0042771A KR100402009B1 (en) | 1999-10-05 | 1999-10-05 | A method for manufacturing a hot rolled sheet steel for the both side enamel coating |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR10-1999-0042771A KR100402009B1 (en) | 1999-10-05 | 1999-10-05 | A method for manufacturing a hot rolled sheet steel for the both side enamel coating |
Publications (2)
Publication Number | Publication Date |
---|---|
KR20010035962A KR20010035962A (en) | 2001-05-07 |
KR100402009B1 true KR100402009B1 (en) | 2003-10-17 |
Family
ID=19613979
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
KR10-1999-0042771A KR100402009B1 (en) | 1999-10-05 | 1999-10-05 | A method for manufacturing a hot rolled sheet steel for the both side enamel coating |
Country Status (1)
Country | Link |
---|---|
KR (1) | KR100402009B1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100506634B1 (en) * | 2002-10-01 | 2005-08-11 | 주식회사 포스코 | Manufacturing method of hot coil for enameled ironware |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR890010236A (en) * | 1987-12-28 | 1989-08-07 | 정명식 | Manufacturing method of continuous annealing enamel steel sheet with excellent formability and enamel |
JPH02305926A (en) * | 1989-05-17 | 1990-12-19 | Nippon Steel Corp | Production of hot rolled steel sheet for enamel |
JPH06192727A (en) * | 1992-12-24 | 1994-07-12 | Sumitomo Metal Ind Ltd | Production of aluminum killed cold rolled steel sheet for enameling |
JPH06279865A (en) * | 1993-03-29 | 1994-10-04 | Sumitomo Metal Ind Ltd | Production of cold rolled steel sheet for porcelain enameling |
KR950011622A (en) * | 1993-10-14 | 1995-05-15 | 조말수 | Manufacturing method of hot rolled steel sheet without fish scale defect |
JPH10168522A (en) * | 1996-12-10 | 1998-06-23 | Nkk Corp | Production of cold rolled steel sheet for porcelain enameling, excellent in fishscale resistance |
-
1999
- 1999-10-05 KR KR10-1999-0042771A patent/KR100402009B1/en not_active IP Right Cessation
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR890010236A (en) * | 1987-12-28 | 1989-08-07 | 정명식 | Manufacturing method of continuous annealing enamel steel sheet with excellent formability and enamel |
JPH02305926A (en) * | 1989-05-17 | 1990-12-19 | Nippon Steel Corp | Production of hot rolled steel sheet for enamel |
JPH06192727A (en) * | 1992-12-24 | 1994-07-12 | Sumitomo Metal Ind Ltd | Production of aluminum killed cold rolled steel sheet for enameling |
JPH06279865A (en) * | 1993-03-29 | 1994-10-04 | Sumitomo Metal Ind Ltd | Production of cold rolled steel sheet for porcelain enameling |
KR950011622A (en) * | 1993-10-14 | 1995-05-15 | 조말수 | Manufacturing method of hot rolled steel sheet without fish scale defect |
JPH10168522A (en) * | 1996-12-10 | 1998-06-23 | Nkk Corp | Production of cold rolled steel sheet for porcelain enameling, excellent in fishscale resistance |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100506634B1 (en) * | 2002-10-01 | 2005-08-11 | 주식회사 포스코 | Manufacturing method of hot coil for enameled ironware |
Also Published As
Publication number | Publication date |
---|---|
KR20010035962A (en) | 2001-05-07 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
KR101852277B1 (en) | Cold rolled steel sheet, method of manufacturing and vehicle | |
EP3508605B1 (en) | Cold-rolled high-strength steel plate having excellent phosphating performance and formability and manufacturing method therefor | |
CN110777290B (en) | Hot-dip galvanized aluminum-magnesium high-strength steel, preparation method and application | |
CN110100031B (en) | High-strength hot-rolled steel sheet, cold-rolled steel sheet, high-strength hot-dip galvanized steel sheet, and methods for producing these | |
KR20140116936A (en) | Hot-dip galvanized steel sheet and production method therefor | |
JP6475840B2 (en) | High-strength hot-dip galvanized steel sheet excellent in surface quality, plating adhesion, and formability, and its manufacturing method | |
KR20210002639A (en) | Steel plate and enamel products | |
US11401567B2 (en) | Manufacturing method of steel sheet | |
CN113637905B (en) | Low-cost weathering steel for 310MPa cold-rolled automobile and preparation method thereof | |
JPH0310048A (en) | Steel sheet for porcelain enameling having excellent fishscale resistance and press formability and its manufacture | |
KR101647223B1 (en) | Method for manufacturing high strength galvanized steel sheet having excellent surface property and coating adhesion | |
CN113637901A (en) | Cold-rolled automobile economic weathering steel with yield strength of 280MPa and production method thereof | |
KR20150123903A (en) | High-strength hot-dip galvanized steel sheet and method for manufacturing same | |
KR100334679B1 (en) | Steel for Coating Excellent in good Durability of Coated Film, and Manufacturing Process Thereof | |
KR100402009B1 (en) | A method for manufacturing a hot rolled sheet steel for the both side enamel coating | |
JP3965792B2 (en) | Manufacturing method of steel sheet with excellent surface properties | |
KR970011629B1 (en) | Method of manufacturing cold rolling sheet | |
KR100470056B1 (en) | A cold rolled steel sheet for direct-on enamel applications with excellent adherence | |
CN113637904B (en) | 340 MPa-grade cold-rolled low-cost weathering steel for automobiles and manufacturing method thereof | |
KR100402001B1 (en) | A method for manufacturing the cold rolled sheet steel for the direct-on enamel coating | |
KR100401981B1 (en) | A method for manufacturing two-sides enameled and hot-rolled steel sheets having superior fish scale resistance | |
KR100506634B1 (en) | Manufacturing method of hot coil for enameled ironware | |
JP4940691B2 (en) | High-strength cold-rolled steel sheet with excellent post-painting corrosion resistance and its manufacturing | |
KR100361753B1 (en) | Method for manufacturing hot rolled enamel steel sheet using thin slab direct rolling | |
KR100470669B1 (en) | A method for manufacturing high strength cold-rolled enamel steel sheet with superior fishscale resistance |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A201 | Request for examination | ||
E701 | Decision to grant or registration of patent right | ||
GRNT | Written decision to grant | ||
LAPS | Lapse due to unpaid annual fee |