KR930002739B1 - Method for making aluminium-killed cold-rolled steel having a good forming property - Google Patents

Method for making aluminium-killed cold-rolled steel having a good forming property Download PDF

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KR930002739B1
KR930002739B1 KR1019910005864A KR910005864A KR930002739B1 KR 930002739 B1 KR930002739 B1 KR 930002739B1 KR 1019910005864 A KR1019910005864 A KR 1019910005864A KR 910005864 A KR910005864 A KR 910005864A KR 930002739 B1 KR930002739 B1 KR 930002739B1
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slab
rolled steel
tungsten
carbon
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KR920019947A (en
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전광근
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포항종합제철 주식회사
정명식
재단법인 산업과학기술연구소
백덕현
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    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips

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  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
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  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

A soft cold rolled steel plate, employing as the starting material a slab which is composed of the low carbon steel added a little content of tungsten, comprises 0.02-0.1 wt.% carbon, less than 0.3 wt.% manganese, less than 0.02 wt.% sulphur, less than 0.005 wt.% nitrogen, 0.03-0.07 wt.% aluminum, 0.01-0.20 wt.% tungsten, inevitable impurities and the balance of iron. The cold rolled steel is prepared by (a) soaking the slab continuously casted by Al-killed method at 1050-1150 deg.C, (b) finish rolling the slab at the temperature of Ar3, (c) after hot rolling to wind the slab steel at 650-750 deg.C, and cold rolling, and (d) continuously tempering at 800-850 deg.C.

Description

성형성이 우수한 Al-킬드 냉연강판의 제조방법Manufacturing method of Al-killed cold rolled steel sheet with excellent formability

본 발명은 자동차용 연질 냉연강판으로 사용되는 알루미늄(Al)-킬드(killed) 냉연강판의 제조방법에 관한 것으로, 보다 상세히는 0.02% 이상의 저탄소강에 텅스텐이 소량 첨가된 슬라브를 Al-킬드법으로 연속주조(이하, "연주"라 칭함)에 의해 열간압연하고 냉각 압연한 후 연속소둔함으로써, 성형성이 우수한 연질 냉연강판을 제조하는 방법에 관한 것이다.The present invention relates to a method for manufacturing an aluminum (Al) -killed cold rolled steel sheet used as a soft cold rolled steel sheet for automobiles, and more particularly, to a slab in which a small amount of tungsten is added to a low carbon steel of 0.02% or more by Al-kill method. The present invention relates to a method for producing a soft cold rolled steel sheet excellent in formability by hot rolling, continuous rolling, and subsequent annealing by continuous casting (hereinafter referred to as "casting").

이러한 기술과 관련된 합금원소를 첨가하여 성형성을 향상시키는 종래의 냉연강판으로는 저탄소 림드강에 소량의 텅스텐을 첨가하는 방법(The Journal of the Australian Institute of Metal Vol 17, 1972 No.3)과 극저탄소강에 티타늄(일특개 소 60-82616호)이나 니오비움(일특개 소 54-1245호)등과 같은 탄화물, 질화물을 형성하기가 용이한 합금원소를 첨가하는 방법을 들 수 있다. 전자의 탕스텐을 첨가하는 방법은 제강후 조괴에 의하여 슬라브를 제조하고 냉간압연후 재결정소둔으로는 상소둔을 채택함으로서 공정이 복잡하고 처리시간이 오래걸릴 뿐만 아니라 제품의 재질이 길이 방향으로 편차가 큰 단점이 있다. 또한, 후자의 티타늄이나 니오비움(합금원소)을 첨가하는 방법은 합금원소의 첨가에 의한 석출물의 크기를 제어하고, 또한 효과적으로 강중에 고용탄소나 고용질소를 소거시키기 위하여 합금 원소와(탄소+질소)의 함량비가 원자비로 약 1.0정도가 되도록 티타늄이나 니오비움을 첨가하고 있다. 따라서, 티타늄이나 니오비움을 첨가한 냉연강판의 경우 탄소함량이 높으면 소요되는 합금원소량이 증가하여 원가상승의 요인이 되므로 통상 극저탄소강을 이용하고 있는 실정이며, 이때 제강에서 제어가능한 탄소함량의 수준이 최저 0.015~0.025%이므로 별도의 탈탄 공정을 거쳐야 한다. 따라서, 추가되는 탈탄공정의 처리비용의 증가와 이 공정처리의 추가로 인한 생산성이 저하하는 문제점이 있다. 이에 본 발명의 목적은 상기 문제점을 해결하기 위한 것으로, 0.02wt% 이상의 저탄소강에 텅스텐을 소량첨가하여 제강후 Al로 탈산함으로써, 종래의 조괴법과는 달리 슬라브제조를 연주화하고자 하는 것이며, 또한 이것에 덧붙여 냉간압연후 연속소둔함으로써 성형이 우수한 Al-킬드 냉연강판을 제공하고자 하는데 있다.Conventional cold rolled steels that improve the formability by adding alloying elements related to this technology include the method of adding a small amount of tungsten to low carbon rim steel (The Journal of the Australian Institute of Metal Vol 17, 1972 No. 3) and the poles. And a method of adding carbides such as titanium (Japanese Patent Application Laid-Open No. 60-82616) or niobium (Japanese Patent Application Laid-Open No. 54-1245) to an alloy element which is easy to form nitride. The method of adding the former tansten is manufactured by slab by steelmaking ingot and adopts annealing for recrystallization annealing after cold rolling, which makes the process complicated and takes a long time to process, and the material of the product varies in the longitudinal direction. There is a big disadvantage. In addition, the latter method of adding titanium or niobium (alloy element) controls the size of precipitates by the addition of alloying elements, and also effectively removes dissolved carbon and solid solution nitrogen in the steel (carbon + nitrogen). Titanium or niobium is added so that the content ratio of c) is about 1.0 in atomic ratio. Therefore, in the case of a cold rolled steel sheet containing titanium or niobium, when the carbon content is high, the amount of alloying elements increases, which causes a cost increase. Therefore, ultra-low carbon steel is usually used. Since the level is at least 0.015 to 0.025%, a separate decarburization process is required. Therefore, there is a problem that the increase in the treatment cost of the additional decarburization process and the productivity due to the addition of this process treatment are lowered. Accordingly, an object of the present invention is to solve the above problems, by adding a small amount of tungsten to 0.02wt% or more of low carbon steel and deoxidizing it to Al after steelmaking, unlike the conventional ingot method, it is intended to regenerate slab production. In addition, it is intended to provide an Al-killed cold rolled steel sheet having excellent molding by continuous annealing after cold rolling.

상기 목적달성을 위해, 본 발명자들은 텅스텐을 소량첨가한 저탄소강을 제강후 Al-killed에 의한 연주(슬라브제조), 열간압연후 고온권취, 냉간압연후 연속소둔에 의하여 본 발명을 완성하였다.In order to achieve the above object, the present inventors completed the present invention by performing low-carbon steel in which tungsten was added in small amounts by steelmaking (slab production), hot rolling after hot rolling, and continuous annealing after cold rolling.

본 발명은 저탄소강에 텅스텐이 소량 첨가되어 제강된 슬라브를 열간압연한후, 냉간압연하고 소둔하는 공정을 포함하여 구성되는 연질냉연강판의 제조방법에 있어서, 상기 슬라브가 중량%로, C : 0.02~0.1%, Mn : 0.3%이하, Al : 0.03~0.07%, P : 0.2%이하, S : 0.02%이하, N : 0.005%이하, Al : 0.03~0.07%, W : 0.01~0.20%, 기타 불가피한 불순물 및 Fe로 조성되고 Al-킬드법에 의해 연속주조되며; 상기 열간압연에 의해 제조된 열연강판이 650~750℃에서 권취되며; 상기 냉연압연된 냉연재가 800~850°의 온도에서 연속소둔됨을 구성의 특징으로 한다.According to the present invention, a method of manufacturing a soft cold rolled steel sheet comprising a step of hot rolling a slab made by adding a small amount of tungsten to a low carbon steel, followed by cold rolling and annealing, wherein the slab is in weight%, C: 0.02 ~ 0.1%, Mn: 0.3% or less, Al: 0.03 ~ 0.07%, P: 0.2% or less, S: 0.02% or less, N: 0.005% or less, Al: 0.03 ~ 0.07%, W: 0.01 ~ 0.20%, etc. Composed of unavoidable impurities and Fe and continuously cast by Al-kill method; The hot rolled steel sheet produced by the hot rolling is wound at 650 ~ 750 ℃; The cold rolled cold rolled material is characterized in that the continuous annealing at a temperature of 800 ~ 850 °.

이하, 본 발명에 대하여 상세히 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail.

상기 슬라브의 탄소함량을 0.02~0.10%로 한정한 것은 0.020%이하에서는 제강공정에서 추가의 탈탄공정을 필요로하는 어려움이 있고, 0.10%를 초과하면 텅스텐에 의한 강중 탄소의 효과적인 소거가 어려워 고용탄소에 의한 성형성 저하가 일어나고, 더욱이 이러한 고용탄소를 완전히 제거하기 위해 필요한 합금원소의 첨가량이 과다해지기 때문이다. 텅스텐이 첨가된 저탄소강에 있어서, 나타나는 탄화물은(Fe, W)3C, W2C 등이 있으며 본 발명강에서 탄소함량에 비하여 화학양론비 이하의 텅스텐을 첨가하는 경우에는 주로(Fe, W)3C가 나타나지만 고온에서 과시효를 하는 경우에는 약간의 미세한 W2C가 형성되기도 한다.The carbon content of the slab is limited to 0.02 to 0.10%, which is difficult to require additional decarburization in the steelmaking process below 0.020%, and when it exceeds 0.10%, it is difficult to effectively remove carbon in the steel by tungsten, and thus the solid carbon This is because moldability deterioration occurs, and the amount of addition of alloying elements required to completely remove such solid solution carbon becomes excessive. In tungsten-added low carbon steels, the carbides represented are (Fe, W) 3 C, W 2 C, and the like. In the present invention, when tungsten with a stoichiometric ratio less than that of carbon is added (Fe, W) ) 3 C appears, but when overaged at high temperatures, some fine W 2 C is formed.

또한, Mn량을 0.3%이하로 한정한 것은 Mn이 강중에서 탄소와 사이에 인력작용을 함으로써(Fe, W)3C의 형성을 억제하여 성형성을 감소시키는 집합조직을 발달시키기 때문이다. 또한, P량을 0.02%이하로 한정한 것은 점용접성, 도장성저하 및 2차 가공시 입계취성 발생을 일으키고 고용강화 효과에 의하여 항복강도, 인장강도를 상승시키는 원소이기 때문이다. S는 열간압연시 적열취성에 의한 코일 가장자리 균열을 발생하는 원소이나, Mn에 의하여 S를 MnS 형태로 석출시키면 균열의 발생을 방지할 수 있다. 따라서 첨가하는 Mn이 강중 산소와 결합하고 난 나머지 함량을 고려하여 그 함량은 0.020%이하로 하면된다. N은 강판의 강도 증가 및 연신율 저하 효과가 크고 상온에서 시효를 일으키는 원소이기 때문에 강중에서 질화물로서 석출시키는 것이 재질상 유리하며 본 발명의 경우 연주화를 위하여 Al를 제강후 탈산제로서 투입하기 때문에 강중의 Al은 N과 결합력이 강하고 AlN을 형성하기 쉽다. 따라서 Al에 의해 질화물로 완전히 석출할 수 있는 범위이내로 제한하는 것이 바람직하나 하기 Al양을 고려하여 설정하면 된다. Al은 0.07%이상이면 알루미늄 산화물에 의한 강판의 표면결함을 발생시키는 문제점이 있고 0.03%이하이면 강중 N를 충분히 석출시키기 곤란함으로 Al은 0.05~0.07%, 이때 N은 50ppm이하로 한정하는 것이 바람직하다.Also, the Mn amount is restricted to less than 0.3% is due to the development of the texture of the Mn by the force acting between the carbon to suppress the formation of (Fe, W) C 3 decreases formability in steel. In addition, the amount of P is limited to 0.02% or less because it is an element that causes spot weldability, poor paintability and grain brittleness during secondary processing and increases yield strength and tensile strength by solid solution strengthening effect. S is an element that causes coil edge cracking due to red hot brittleness during hot rolling, but when S is precipitated in the form of MnS by Mn, cracking can be prevented. Therefore, the amount of Mn added should be less than 0.020% in consideration of the remaining content combined with oxygen in the steel. Since N is an element that increases the strength of the steel sheet and decreases the elongation rate and causes aging at room temperature, it is advantageous in terms of material to precipitate as nitride in the steel.In the present invention, Al is added as a deoxidizer after steelmaking for reoxidation. Al has a strong bonding force with N and is easy to form AlN. Therefore, it is preferable to limit within the range that can be completely precipitated as nitride by Al, but may be set considering the following Al amount. If Al is 0.07% or more, there is a problem of generating surface defects of the steel sheet by aluminum oxide. If Al is less than 0.03%, it is difficult to sufficiently precipitate N in the steel.Al is preferably 0.05 to 0.07%, and N is preferably limited to 50 ppm or less. .

한편, W은 C의 결합하는 원소로서 제강-열연간에(Fe, W)3C로 석출함으로써 고용탄소에 의한 성형성 저하를 방지하고 연신율 증가를 목적으로 첨가하였으며 W을 과잉첨가할 경우에는 조대 텅스텐 탄화물 형성에 의하여 재질이 열화된다. 따라서, W의 첨가량은 0.01~0.20%에서 첨가하는 것이 바람직하며, W3C를 기준으로 할 경우에는(W at%)/(C at%)=0.04~0.10의 범위로 하는 것이 더욱 바람직하다.On the other hand, W is a binding element of C, which is precipitated as 3 C between steelmaking and hot rolling (Fe, W) to prevent formability deterioration due to solid solution carbon and to increase elongation. The material is degraded by the formation of carbides. Therefore, the amount of W added is preferably added at 0.01 to 0.20%, and more preferably at (W at%) / (C at%) = 0.04 to 0.10 when based on W 3 C.

한편, 본 발명에 있어서, 슬라브 가열온도는 1050~1150℃로 하는 것이 바람직한데, 이는 강중에 이미 석출하고 있는 WC, (Fe, W)3C등과 같은 W계통의 석출물들이 이 온도역에서는 완전히 용해되지 않으며 미용해된 석출물들은 그후 계속되는 열간압연시 조대화되고 일부 잔류한 W은 압연후 Fe3C의 Fe와 부분적으로 교체되어(Fe, W)3C를 형성함으로써, 소둔판의 (111) 집합조직 성분의 발달을 도모하여 성형성 향상을 유리하게 하기 때문이다. 또한, 열간압연 마무리온도는 균일한 정립의 재결정조직을 얻기 위하여 Ar3직상의 온도로 하는 것이 바람직하다. 또한, 권취온도는 열연판의 결정입도와 석출분포에 미치는 영향이 크고, 결정입도 및 석출물 분포가 성형성에 직접적인 관계가 있는데, 본 발명에서의 주된 석출물은(Fe, W)3C로서 이 석출물은 열연후 권취시 조대화하기 용이한 석출물이므로 효과적인 석출물 크기를 얻기 위하여 600~700℃에서 권취하는 것이 가공성을 향상시키는데 필요하다. 또한, 냉간압연후 재결정 소둔은 가열속도가 5℃/초로 매우 빠르고 소둔후 급냉-과시효처리가 가능한 연속소둔을 적용하는 것이 바람직한데, 이때 소둔온도는 재결정 완료후 입성장이 충분히 일어날 수 있도록 800~850℃로 하는 것이 바람직하다.On the other hand, in the present invention, the slab heating temperature is preferably set to 1050 ~ 1150 ℃, which W precipitates, such as WC, (Fe, W) 3 C already precipitated in the steel is completely dissolved in this temperature range. Undissolved precipitates are then coarsened during subsequent hot rolling and some remaining W is partially replaced with Fe 3 C Fe after rolling (Fe, W) to form 3 C, thereby forming a (111) set of annealing plates. This is because the development of tissue components is facilitated and the moldability is improved. In addition, the hot rolling finish temperature is preferably set to a temperature directly above Ar 3 in order to obtain a uniform grain recrystallization structure. In addition, the coiling temperature has a large influence on the crystal grain size and the precipitation distribution of the hot rolled sheet, the crystal grain size and precipitate distribution has a direct relationship to the formability, the main precipitate in the present invention is (Fe, W) 3 C as the precipitate Since it is easy to coarse when winding after hot rolling, it is necessary to wind up at 600 ~ 700 ℃ to improve the processability in order to obtain an effective precipitate size. In addition, the recrystallization annealing after cold rolling, it is desirable to apply a continuous annealing capable of very fast heating rate of 5 ℃ / second after quenching and over-aging treatment, wherein the annealing temperature is 800 ~ to ensure sufficient grain growth after recrystallization complete It is preferable to set it as 850 degreeC.

이하, 실시예를 통하여 본 발명을 상세히 설명한다.Hereinafter, the present invention will be described in detail through examples.

[실시예]EXAMPLE

하기표 1과 같은 화학성분을 가진 진공용해한 슬라브를 이용하여 열간압연전 가열온도를 1100℃에서 1시간 유지한 후 열간압연을 890℃에서 마무리하여 3.2mm의 열연판을 제조한 다음 권취공정을 재현하기 위해 700℃에서 1시간 유지후 노냉하였다. 그후 강판표면의 스케일을 산세에 의하여 제거한 다음 압하율 75%로 냉간압연하였다. 연속소둔조건은 가열속도 5℃/초로 830℃까지 가열하여 40초동안 유지한 뒤 680℃까지 5℃/초로 서냉하고 이어서 400℃까지 급냉한 다음 과시효처리를 위하여 400℃에서 350℃까지 15℃/분의 냉각속도로 노냉하였다.Using a vacuum-dissolved slab having the chemical composition as shown in Table 1, after maintaining the heating temperature before hot rolling at 1100 ° C. for 1 hour, the hot rolling was finished at 890 ° C. to produce a 3.2 mm hot rolled sheet and then reproduce the winding process. In order to maintain the temperature at 700 ° C. for 1 hour, the furnace was cooled. Thereafter, the scale of the steel plate surface was removed by pickling and then cold rolled to a reduction ratio of 75%. Continuous annealing conditions were maintained at 830 ° C. at a heating rate of 5 ° C./sec for 40 seconds, then slowly cooled to 5 ° C./sec up to 680 ° C., followed by quenching to 400 ° C., and 15 ° C. from 400 ° C. to 350 ° C. for overaging treatment. The furnace was cooled at a cooling rate of / min.

[표 1]TABLE 1

Figure kpo00001
Figure kpo00001

이렇게 하여 제조된, 탄소함량에 따른 텅스턴 첨가재(본 발명재)와 비교재에 대한 기계적 성질을 하기 표 2에 나타내었다.The mechanical properties of the tungsten additive (inventive material) and the comparative material prepared in this way are shown in Table 2 below.

[표 2]TABLE 2

Figure kpo00002
Figure kpo00002

γ값 : 성형성 지수를 나타내는 랭크 포오드값(lank ford value)γ value: rank ford value representing the formability index

상기 표 2에 의하면, 본 발명재는 항복강도 및 인장강도가 비교재에 비해 열화하지 않으면서도 연신율 및 γ값이 합금원소를 첨가하지 않는 비교재에 비하여 우수한 결과를 나타냄을 알 수 있다. 또한, 텅스텐을 첨가한 본 발명재의 경우 텅스텐 대 탄소비가 클수록 항복강도가 감소하고 가공성이 향상됨을 알 수 있다.According to the above Table 2, it can be seen that the present invention exhibits excellent results compared to the comparative material in which the yield strength and the tensile strength are not deteriorated in comparison with the comparative material, but the elongation and? Value are not added with the alloying element. In addition, it can be seen that the greater the tungsten-to-carbon ratio of the present invention with tungsten added, the lower the yield strength and the improved workability.

상술한 바와같이, 본 발명의 제조방법에 의하면 종래의 냉연강판 제조방법, 즉 티타늄(Ti)이나 니오비움(Nb)을 첨가하여 강종의 칩입형원소인 탄소나 질소와 결합하게 함으로써 고용상태의 탄소나 질소를 제거하는 종래 방법에 비해 탄소함량의 제약이 비교적 적은 중저탄소강 수준에서도 양호한 성형성의 확보가 가능하며, 제강공정에서 RH-OB와 같은 탈탄과정의 생략이 가능함으로써 처리비용 저감 및 공정처리시간을 단축 할 수 있는 효과가 있다. 또한, 본 발명은 알루미늄(Al)에 의해 탈산함으로써 제강후 연주가 가능하고 연속소둔을 채택함으로써 생산성을 향상시킬 수 있는 효과가 있다.As described above, according to the manufacturing method of the present invention, a conventional cold rolled steel sheet manufacturing method, that is, titanium (Ti) or niobium (Nb) is added to bond with carbon or nitrogen, which is a chip-type element of steel, to form carbon in solid solution. In addition, it is possible to secure good formability even at the low and low carbon steel level where the carbon content is relatively low compared to the conventional method of removing nitrogen, and the decarburization process such as RH-OB can be omitted in the steelmaking process, thereby reducing the processing cost and processing time. There is an effect that can shorten. In addition, the present invention has the effect that can be performed after steelmaking by deoxidizing with aluminum (Al), and productivity can be improved by adopting continuous annealing.

Claims (1)

저탄소강에 텅스텐이 소량 첨가된 슬라브를 출발소재로 하여 연질냉연강판을 제조하는 방법에 있어서, 중량%로, C : 0.02~0.1%, Mn : 0.3%이하, P : 0.02%이하, S : 0.02%이하, N : 0.005%이하, Al : 0.03~0.07%, W : 0.01~0.20%, 기타 불기피한 불순물 및 Fe로 조성되고 Al-킬드법에 의해 연속주조된 슬라브를 1050~1150℃에서 균열처리하고 Ar3직상의 온도에서 마무리 압연하며 650~750℃에서 권취하는 열간압연을 실시한 후 냉간압연을 실시하고 800~850℃의 온도에서 연속 소둔함을 특징으로 하는 성형성이 우수한 Al-킬드 냉연강판의 제조방법.In the method for producing a soft cold rolled steel sheet using a slab containing a small amount of tungsten in low carbon steel as a starting material, in weight%, C: 0.02 to 0.1%, Mn: 0.3% or less, P: 0.02% or less, S: 0.02 % Or less, N: 0.005% or less, Al: 0.03 ~ 0.07%, W: 0.01 ~ 0.20%, other unavoidable impurities and slabs made of Fe and continuously cast by Al-kill method at 1050 ~ 1150 ℃ Al-killed cold rolling with excellent moldability, characterized in that it is treated, finished and rolled at a temperature directly above Ar 3, hot rolled at 650 to 750 ° C., followed by cold rolling, and continuous annealing at a temperature of 800 to 850 ° C. Method of manufacturing steel sheet.
KR1019910005864A 1991-04-12 1991-04-12 Method for making aluminium-killed cold-rolled steel having a good forming property KR930002739B1 (en)

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