KR20120071587A - Method for manufacturing bearing steel wire rod having excellent durability and abrasion resistance - Google Patents

Method for manufacturing bearing steel wire rod having excellent durability and abrasion resistance Download PDF

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KR20120071587A
KR20120071587A KR1020100133188A KR20100133188A KR20120071587A KR 20120071587 A KR20120071587 A KR 20120071587A KR 1020100133188 A KR1020100133188 A KR 1020100133188A KR 20100133188 A KR20100133188 A KR 20100133188A KR 20120071587 A KR20120071587 A KR 20120071587A
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steel
molten steel
wire rod
temperature
bearing steel
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KR1020100133188A
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KR101242987B1 (en
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이환희
최진두
정성한
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주식회사 포스코
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0025—Adding carbon material
    • 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
    • B21B1/16—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 wire rods, bars, merchant bars, rounds wire or material of like small cross-section
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

PURPOSE: A method for manufacturing a bearing steel wire rod is provided to obtain a bearing steel wire rod with excellent durability and abrasion resistance by properly controlling the tapping temperature from a converter, the heating-up time of an LF(Ladle Furnace) process, and the molten steel circulation time of an RH(Ruhrstahl-Heraeus) process. CONSTITUTION: A method for manufacturing a bearing steel wire rod having excellent durability and abrasion resistance comprises a step of making molten steel, which comprises C of 0.9-1.4 weight%, Si of 0.15-0.25 weight%, Mn of 0.25-0.45 weight%, Cr of 1.3-1.6 weight%, P of 0.02 weight% or less, S of 0.008 weight% or less, and Fe and inevitable impurities of the remaining amount, in a converter, a step of tapping the molten steel at a temperature of 1630-1680°C, performing an LF process with a heating-up time of 10-19 minutes, performing an RH process with a molten steel circulation time of 25-35 minutes and casting the molten steel, and a step of rolling the cast billet into a wire rod.

Description

내구성 및 내마모성이 우수한 베어링강 선재의 제조방법{Method for Manufacturing Bearing Steel Wire Rod Having Excellent Durability and Abrasion Resistance}Method for Manufacturing Bearing Steel Wire Rod Having Excellent Durability and Abrasion Resistance}

본 발명은 자동차 및 일반 산업용 베어링 등을 만드는데 사용되는 베어링 강 선재를 제조하는 방법에 관한 것으로서, 보다 상세하게는 개재물 품질을 개선하여 내구성 및 내마모성을 향상시킨 베어링강 선재를 제조하는 방법에 관한 것이다.
The present invention relates to a method of manufacturing a bearing steel wire used to make bearings for automobiles and general industrial purposes, and more particularly, to a method of manufacturing bearing steel wire having improved durability and wear resistance.

베어링강 선재는 고온, 고압의 조건에서 지속적으로 적용되는 하중을 견디어 내야 하기 때문에 내구성과 내마모성이 피로수명을 결정짓는 매우 중요한 인자이다. Since the bearing steel wire has to withstand loads applied continuously under high temperature and high pressure conditions, durability and wear resistance are very important factors for determining fatigue life.

내구성 및 내마모성을 저하시키는 주요 인자로는 비금속개재물과 중심부의 거대 탄화물이 있는데, 그 중에서도 개재물 품질은 베어링강의 피로수명과 매우 밀접한 상관관계를 가지고 있음이 여러 연구 결과에서 보고되었다. Major factors that lower durability and abrasion resistance include nonmetallic inclusions and large carbides in the core, among which, the quality of inclusions has been closely correlated with the fatigue life of bearing steel.

개재물 품질을 나타내는 가장 대표적인 지표로는 제품 내 존재하는 산소의 총 량을 의미하는 T[O]가 있으며, 대부분의 글로벌(Global) 베어링강 고객사에서는 T[O] 실적을 바탕으로 베어링강 품질의 우열을 분류하고 있다. The most representative indicator of inclusion quality is T [O], which means the total amount of oxygen present in the product, and most global bearing steel customers have superior bearing steel quality based on T [O] performance. Is classified.

이 때문에 얼마나 T[O]가 낮은 베어링강을 생산할 수 있느냐는 강 제조사(Steelmaker)의 제강기술을 판가름하는 데 합리적인 기준이 되고 있는 실정이다.For this reason, how much low T [O] can produce bearing steel is a reasonable criterion for determining steelmaker's steelmaking technology.

지금까지 알려진 T[O]를 낮추기 위한 대표적인 방법으로는 전로 출강 시, 조제재 및 알루미나 투입의 패턴을 적절히 제어하는 방법, 2차 정련 시 슬래그(slag) 염기도를 제어하는 방법, RH 진공처리시간 및 용강체류시간을 확보하는 방법등이 있다.Representative methods for lowering the T [O] known to date include a method of properly controlling the pattern of preparation and alumina input during the tapping of the converter, a method of controlling the slag basicity during the secondary refining, the RH vacuum treatment time, There are ways to secure molten steel stay time.

그러나, 이러한 방법을 적용하는 경우에도 베어링강의 T[O] 수준이 약 5.5~6ppm 이므로 여전히 충분한 내구성 및 내마모성을 갖는 베어링 강의 제조는 곤란하다는 문제점이 있다.However, even when applying this method, since the T [O] level of the bearing steel is about 5.5 to 6 ppm, there is a problem that it is difficult to manufacture the bearing steel still having sufficient durability and wear resistance.

따라서, 충분한 내구성 및 내마모성을 갖는 베어링 강을 제조하기 위한 새로운 기술의 개발이 요구되고 있다.
Therefore, there is a need for the development of new technologies for producing bearing steels with sufficient durability and wear resistance.

본 발명은 전로로부터의 출강온도, LF(Ladle Furnace) 승온시간 및 RH 공정의 용강환류시간을 적절히 제어함으로써 내구성 및 내마모성이 우수한 베어링 강 선재를 제조하는 방법을 제공하고자 하는 것이다.
The present invention is to provide a method for producing a bearing steel wire having excellent durability and wear resistance by appropriately controlling the tapping temperature from the converter, Ladle Furnace temperature rise time and the molten steel reflux time of the RH process.

본 발명의 일 측면에 의하면, 전로에서, 중량%로, C: 0.9?1.4%, Si: 0.15?0.25%, Mn: 0.25?0.45%, Cr: 1.3?1.6%, P: 0.02%이하, S: 0.008%이하, 나머지 Fe 및 기타 불가피한 불순물로 조성된 용강을 제조한 후, 1630℃이상의 온도에서 출강하고, LF 설비에서 승온시간을 19분이하로 하여 LF처리를 행하고, 25분이상의 용강환류시간 조건으로 RH 공정을 행한 후, 주조한 다음, 강편압연하고, 선재압연하는 내구성 및 내마모성이 우수한 베어링 강 선재의 제조방법이 제공된다.
According to an aspect of the present invention, in the converter, in weight%, C: 0.9 to 1.4%, Si: 0.15 to 0.25%, Mn: 0.25 to 0.45%, Cr: 1.3 to 1.6%, P: 0.02% or less, S : Manufactured molten steel of 0.008% or less, remaining Fe and other unavoidable impurities, and tapping at a temperature of 1630 ° C or higher, performing LF treatment with a temperature rising time of 19 minutes or less in an LF facility, and molten steel reflux time condition of 25 minutes or more. After the RH process is carried out, the casting, the steel sheet is rolled, and the wire rod is rolled. A method for producing a bearing steel wire having excellent durability and wear resistance is provided.

상술한 바와 같이, 본 발명에 의하면, 종래방법에 비하여 내구성 및 내마모성이 우수한 베어링강 선재를 제조할 수 있다.
As described above, according to the present invention, it is possible to produce a bearing steel wire rod excellent in durability and wear resistance as compared with the conventional method.

도 1은 본 발명에 부합되는 베어링 강 선재의 제조공정의 일례의 일부를 나타내는 공정개략도
도 2는 본 발명 및 비교방법의 공정 단계 별 용강온도변화를 나타내는 그래프1 is a process schematic diagram showing a part of an example of a manufacturing process of a bearing steel wire according to the present invention;
Figure 2 is a graph showing the temperature change of the molten steel for each process step of the present invention and comparative method

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

본 발명은 중량%로, C: 0.9?1.4%, Si: 0.15?0.25%, Mn: 0.25?0.45%, Cr: 1.3?1.6%, P: 0.02%이하, S: 0.008%이하, 나머지 Fe 및 기타 불가피한 불순물로 조성되는 베어링 선재에 있어서 내구성 및 내마모성을 보다 향상시키고자 하는 것으로서, 이를 위하여 본 발명에서는 전로로부터의 출강온도, LF 승온시간 및 RH 공정의 용강환류시간을 적절히 제어하는 것이다.
In the present invention, by weight%, C: 0.9 to 1.4%, Si: 0.15 to 0.25%, Mn: 0.25 to 0.45%, Cr: 1.3 to 1.6%, P: 0.02% or less, S: 0.008% or less, remaining Fe and In order to further improve the durability and wear resistance in the bearing wires composed of other unavoidable impurities, in the present invention, to control the tapping temperature from the converter, the LF temperature rise time and the molten steel reflux time of the RH process.

먼저, 강 선재의 조성에 대하여 설명한다. 아래 각 성분의 함량은 중량%를 나타낸다.
First, the composition of the steel wire rod will be described. The content of each component below represents the weight percentage.

탄소(C): 0.9~1.4%Carbon (C): 0.9-1.4%

탄소는 소재의 강도를 확보하기 위하여 첨가되는 필수적인 원소이다. 상기 탄소의 함량이 0.9% 미만인 경우에는 강선재에 요구되는 최소강도를 확보할 수 없으며, 그 함량이 1.4%를 초과하는 경우에는 초석 세멘타이트의 억제가 불가능하여 소재의 연성이 현저하게 감소한다. Carbon is an essential element added to secure the strength of the material. If the carbon content is less than 0.9%, it is impossible to secure the minimum strength required for the steel wire, and if the content is more than 1.4%, it is impossible to suppress the cementite cementite and the ductility of the material is significantly reduced.

따라서, 상기 C의 함량은 0.9~1.4%로 제한하는 것이 바람직하며, 보다 바람직한 탄소의 함량은 0.96~1.02%이다.
Therefore, the content of C is preferably limited to 0.9 to 1.4%, and more preferable content of carbon is 0.96 to 1.02%.

실리콘(Cr): 0.15~0.25%Silicon (Cr): 0.15 to 0.25%

실리콘은 대표적인 페라이트 형성 원소(Ferrite former)로 철원자에 비해 원자크기가 작아 상변태 시 열변형량을 최소화할 수 있다. 또한, 실리콘은 세멘타이트 내에 고용도가 거의 없으며, 재료내부의 탄소 원자의 활성(activity 혹은 chemical potential)을 크게 향상시키는 원소로서, 페라이트 상에만 선택적으로 농축되어 사용 중 세멘타이트의 고온 안정성을 향상시키는, 즉 성장속도를 크게 지연시키는 효과가 있다. Silicon is a representative ferrite former, and its atomic size is smaller than that of iron atoms, thereby minimizing thermal strain during phase transformation. In addition, silicon has little solubility in cementite and is an element that greatly enhances the activity (chemical or activity) of carbon atoms in the material, and is selectively concentrated only on ferrite to improve the high temperature stability of cementite during use. In other words, the growth rate is greatly delayed.

상기 실리콘의 함량이 0.15%미만인 경우에는 상기한 첨가효과를 충분히 달성할 수 없고, 0.25%를 초과하는 경우에는 선재압연 후 냉각시 탈탄이 발생될 우려가 있으므로, 그 함량은 0.15~0.25%로 제한하는 것이 바람직하다.
If the silicon content is less than 0.15%, the above additive effects cannot be sufficiently achieved. If the silicon content is more than 0.25%, decarburization may occur during wire rolling after cooling. Therefore, the content is limited to 0.15 to 0.25%. It is desirable to.

망간(Mn): 0.25~0.45%Manganese (Mn): 0.25-0.45%

망간은 강선재 내에 존재할 경우 강선재의 소입성을 향상시켜 강도를 확보하는데 유익한 원소이다. 상기 Mn의 함량이 0.25% 미만인 경우에는 요구되는 충분한 강도 및 소입성을 얻기 어렵고, 0.45%를 초과하는 경우에는 인성이 저하된다. 따라서, 상기 Mn의 함량은 0.25~0.45%로 제한하는 것이 바람직하다.
Manganese is an element that is beneficial in securing strength by improving the hardenability of steel wire when present in steel wire. When the content of Mn is less than 0.25%, it is difficult to obtain the required strength and quenchability, and when it exceeds 0.45%, the toughness is lowered. Therefore, the content of Mn is preferably limited to 0.25 ~ 0.45%.

크롬(Cr): 1.3~1.6%Chromium (Cr): 1.3-1.6%

크롬은 흑연화, 템퍼 연화성 및 소입성을 확보하는데 유용한 원소로 Cr함량이 1.3% 미만인 경우에는 충분한 템퍼 연화성 및 소입성 등을 확보하기 어렵고 실리콘 첨가에 따른 흑연화를 억제하는 것이 어렵다. Chromium is an element that is useful for securing graphitization, temper softening and hardenability. When Cr is less than 1.3%, it is difficult to secure sufficient temper softening and hardenability, and it is difficult to suppress graphitization due to silicon addition.

또한, 1.6%를 초과하는 경우에는 변형저항성의 저하를 초래하여 오히려 강도저하로 이어질 수 있다. 따라서 상기 Cr의 함량은 1.3~1.6%로 제한하는 것이 바람직하다.
In addition, when the content exceeds 1.6%, the deformation resistance may be lowered, which may lead to a decrease in strength. Therefore, the content of Cr is preferably limited to 1.3 to 1.6%.

인(P): 0.02%이하Phosphorus (P): 0.02% or less

인은 불가피하게 함유되는 불순물 성분으로서, P편석을 발생시켜 내구성을 저하시키므로, 그 함량의 상한은 0.02%로 제한하는 것이 바람직하다.
Phosphorus is an impurity component that is inevitably contained, and thus, P segregation is generated to lower durability. Therefore, the upper limit of the content is preferably limited to 0.02%.

황(S): 0.008%이하Sulfur (S): 0.008% or less

황은 불가피하게 함유되는 불순물 성분으로서, 취성을 증가시켜 크랙발생을 유발시키므로, 그 함량의 상한은 0.008%로 제한하는 것이 바람직하다.
Sulfur is an impurity component inevitably contained, and therefore, brittleness is increased to cause cracking. Therefore, the upper limit of the content is preferably limited to 0.008%.

상기와 같이 조성되는 용강은 2차 정련 과정 및 연주, 강편압연, 선재압연 공정을 거쳐 베어링용 선재로 만들어지게 되는데, 이하에서는 제조공정에 대하여 설명한다.Molten steel is formed as described above is made of a wire rod for the bearing through a secondary refining process and playing, steel sheet rolling, wire rod rolling process, the manufacturing process will be described below.

상기와 같이 조성되는 용강은 도 1에 나타난 바와 같이 P성분 등의 제어를 위해 1600℃이하의 온도로 출강된 다음, 성분, 온도 및 품질 제어를 위해 LF 공정 및 RH 공정을 차례로 거치고, 이후 연주공정을 통해 베어링강 선재를 만들기 위한 주편으로 생산된다. As shown in FIG. 1, the molten steel is pulled out at a temperature of 1600 ° C. or lower for the control of the P component, and then sequentially passed through the LF process and the RH process to control the component, temperature, and quality. Is produced as cast steel for making bearing steel wire.

상기와 같이 제조되는 주편의 품질을 확보하기 위해서는 연주가 시작되는 시점에서 용강 온도를 엄격히 관리하는 것이 필요한데, 베어링강의 경우 P 성분등의 제어를 위해 출강온도가 낮기 때문에 LF 공정에서 전극봉을 이용하여 용강의 온도를 상승시키고 있다. In order to secure the quality of the cast steel as described above, it is necessary to strictly manage the molten steel temperature at the time of the start of the play.In the case of bearing steel, the tap temperature is low for the control of the P component, etc. The temperature is rising.

그러나, 이 과정에서 슬래그의 온도가 초고온으로 상승하기 때문에 레이들의 내화물이 용손되어 외래성 개재물이 유입될 가능성이 증가하게 된다. However, in this process, the temperature of the slag rises to an extremely high temperature, thereby increasing the likelihood that the ladle's refractory is melted and foreign inclusions are introduced.

뿐만 아니라, 슬래그의 온도가 고온이 되면 슬래그내 산소의 용해도가 증가하기 때문에 외부의 산소가 슬래그에 용해되기 시작하고, 이는 다시 용강과의 반응을 통해 용강 내 용존 산소량이 증가하게 된다. In addition, when the temperature of the slag becomes high, the solubility of oxygen in the slag increases, so that external oxygen begins to dissolve in the slag, which increases the amount of dissolved oxygen in the molten steel through reaction with the molten steel.

따라서, 용강 내 산소 함량을 극저로 제한하기 위해서는 LF 공정에서 승온시간을 가능한 한 짧게 가져가는 것이 유리하다. Therefore, to limit the oxygen content in the molten steel to an extremely low, it is advantageous to take the temperature rise time as short as possible in the LF process.

그렇게 하기 위해서는 출강 시 온도를 최대한 높게 조업하는 것이 필요하므로 본 발명에서는 전로 출강 시 용강의 온도를 1630℃ 이상으로 제한한 것이다.In order to do so, it is necessary to operate the temperature as high as possible during tapping, so in the present invention, the temperature of molten steel during tapping of the converter is limited to 1630 ° C or more.

바람직하게는, 상기 전로 출강 시 용강 온도의 상한은 1680℃로 제한하는 것이다.Preferably, the upper limit of the molten steel temperature at the time of tapping the converter is limited to 1680 ° C.

또한, 본 발명에서는 LF 공정에 도착한 용강의 승온시간을 19분이하로 제한한다. 즉, 본 발명에서는 상기한 바와 같이 LF 승온시간을 가능한 짧게 하는 것이 본 발명의 핵심요소중의 하나이기 때문에 연주공정에서 요구하는 최소온도를 확보하기 까지 필요한 승온시간을 19분 이내로 제한한다.In the present invention, the temperature rise time of the molten steel arriving at the LF process is limited to 19 minutes or less. That is, in the present invention, as described above, shortening the LF temperature rise time as much as possible is one of the core elements of the present invention, thereby limiting the temperature increase time required to secure the minimum temperature required in the playing process to 19 minutes or less.

바람직하게는, 상기 승온시간의 하한은 10분으로 제한하는 것이다.Preferably, the lower limit of the temperature increase time is limited to 10 minutes.

또한, 본 발명에서는 RH 공정에서 용강환류시간을 25분이상으로 제한한다.In the present invention, the molten steel reflux time in the RH process is limited to 25 minutes or more.

RH 공정에서는 용강 환류를 통해 용강 내의 산소의 양을 감소시키므로 가능한 한 환류시간을 길게 하는 것이 개재물 품질에 유리하다. The RH process reduces the amount of oxygen in the molten steel through the reflux of the molten steel, so it is advantageous to the inclusion quality to make the reflux time as long as possible.

그러나, 무조건 환류시간을 길게 하면, 설비의 과부하 및 설비 용손으로 인한 대형개재물 발생 등 역효과가 크기 때문에 본 발명에서는 RH 용강환류시간을 25분이상으로 제한한다.However, when the reflux time is unconditionally increased, the RH molten steel reflux time is limited to 25 minutes or more in the present invention because the adverse effects such as the generation of large inclusions due to the overload of the equipment and the loss of equipment are large.

바람직하게는, 상기 RH 용강환류시간의 상한은 35분으로 제한하는 것이다.Preferably, the upper limit of the RH molten steel reflux time is limited to 35 minutes.

이와 같이 정련된 용강은 연주, 강편압연, 선재압연 공정을 거쳐 베어링용 선재로 제조된다.The refined molten steel is manufactured as a wire rod for bearings through a process of rolling, rolling a steel sheet, and rolling a wire.

상기한 연주, 강편압연 및 선재압연은 통상적인 방법에 따라 행한다.The above-described performance, rolling of steel strips, and rolling of wire rods are performed according to a conventional method.

상기와 같이 본 발명에 따라 제조된 선재는 바람직하게는 5.0ppm 이하의 T[O]값(총 산소량)), 보다 바람직하게는 4.5ppm 이하의 T[O]값을 갖는다.As described above, the wire rod prepared according to the present invention preferably has a T [O] value (total amount of oxygen) of 5.0 ppm or less, and more preferably a T [O] value of 4.5 ppm or less.

본 발명에 따라 전로로부터의 출강온도, LF 승온시간 및 RH 공정의 용강환류시간을 적절히 제어함으로써 개재물 품질이 우수한 선재의 제조가 가능하게 되고, 결과적으로 선재의 내구성 및 내마모성을 보다 향상시킬 수 있다.
According to the present invention, by appropriately controlling the tapping temperature from the converter, the LF temperature rise time and the molten steel reflux time of the RH process, it is possible to manufacture a wire rod having excellent inclusion quality, and as a result, the durability and wear resistance of the wire rod can be further improved.

이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.

(실시예)(Example)

하기 표 1과 같은 화학조성을 갖는 용강을 하기 표 2의 조건으로 제조한 다음, 통상의 방법으로 주조, 강편압연, 선재압연을 행하여 선재를 제조한 후, 선재중의 산소의 함량을 측정하고, 그 결과를 하기 표 2에 나타내었다.The molten steel having the chemical composition as shown in Table 1 below was prepared under the conditions of Table 2, and then cast, rolled, rolled the wire in a conventional manner to prepare the wire, and then measured the content of oxygen in the wire, and The results are shown in Table 2 below.

하기 발명강 및 비교강에 대한 공정 단계 별 용강온도변화가 도 2에 개략적으로 나타나 있다.The molten steel temperature change according to process steps for the inventive steels and the comparative steels is schematically shown in FIG. 2.

상기 선재의 산소 함량의 측정은 10mm 이내로 절단하여 이루어졌다.
The oxygen content of the wire rod was measured by cutting within 10 mm.

강종
Steel grade
화학성분(중량%)Chemical composition (% by weight) CC SiSi MnMn PP SS CrCr 비교강1Comparative Steel 1 0.98390.9839 0.2150.215 0.3580.358 0.01040.0104 0.00540.0054 1.341.34 비교강2Comparative Steel 2 0.99920.9992 0.2250.225 0.3650.365 0.01290.0129 0.00490.0049 1.321.32 비교강3Comparative Steel 3 1.01001.0100 0.2170.217 0.3440.344 0.01460.0146 0.00490.0049 1.381.38 발명강1Inventive Steel 1 0.98150.9815 0.2130.213 0.3560.356 0.01340.0134 0.00470.0047 1.351.35 발명강2Inventive Steel 2 0.9980.998 0.2230.223 0.3610.361 0.01020.0102 0.00580.0058 1.341.34 발명강3Invention Steel 3 0.9940.994 0.2080.208 0.3690.369 0.00970.0097 0.00550.0055 1.341.34

강종Steel grade 종점[C](wt%)End point [C] (wt%) 출강온도(℃)Tapping temperature (℃) LF승온시간(분)LF temperature rise time (minutes) RH 공정의 용강환류시간(분)Molten steel reflux time of RH process (min) 평균T[O](ppm)Average T [O] (ppm) 비교강1Comparative Steel 1 0.8050.805 15891589 23.723.7 25.325.3 5.55.5 비교강2Comparative Steel 2 0.6680.668 15781578 23.923.9 2525 6.36.3 비교강3Comparative Steel 3 0.7590.759 15821582 24.124.1 27.227.2 5.15.1 발명강1Inventive Steel 1 0.6980.698 16321632 18.718.7 26.526.5 4.04.0 발명강2Inventive Steel 2 0.7070.707 16351635 17.717.7 25.525.5 4.54.5 발명강3Invention Steel 3 0.7280.728 16311631 16.916.9 2727 4.34.3

상기 표 2에 나타난 바와 같이, 본 발명에 부합되는 전로로부터의 출강온도, LF 승온시간 및 RH 공정의 용강환류시간으로 제조된 발명강(1-3)의 평균 T[O]값은 모두 4.5ppm 이하임에 반하여, 종래방법의 조건으로 제조된 비교강(1-3)의 평균 T[O]값은 모두 5.0ppm이상임을 알 수 있다.As shown in Table 2, the average T [O] value of the invention steel (1-3) manufactured by tapping temperature from the converter according to the present invention, the LF temperature rise time and the molten steel reflux time of the RH process were all 4.5 ppm. On the contrary, the average T [O] values of the comparative steels (1-3) manufactured under the conditions of the conventional method are all 5.0 ppm or more.

발명강(1-3)의 평균 T[O]값과 비교강(1-3)의 것을 비교하면 발명강(1-3)은 비교강(1-3)에 비하여 용존 산소량이 낮아진 것을 확인할 수 있다.  Comparing the average T [O] value of the inventive steel (1-3) with that of the comparative steel (1-3), it can be confirmed that the dissolved steel amount of the invention steel (1-3) is lower than that of the comparative steel (1-3). have.

일반적으로 베어링강 선재에서 측정되는 용존 산소량은 제품 내에 존재하는 개재물의 총량과 비례하여 나타나기 때문에 본 발명에 부합되는 조건으로 생산된 베어링강 선재의 경우 개재물 품질이 우수한 것으포 평가할 수 있다. In general, the amount of dissolved oxygen measured in the bearing steel wire is shown in proportion to the total amount of inclusions present in the product, and thus the quality of the inclusions can be evaluated in the case of the bearing steel wire produced under the conditions according to the present invention.

본 발명으로 미루어 승온을 목적으로 실시하는 LF 공정에서 용강 내 산소 함량을 급격하게 증가시킬 수 있으며, 이 때 증가한 산소의 양이 선재 제품에까지 영향을 주고 있음을 알 수 있다. In view of the present invention, it is possible to rapidly increase the oxygen content in the molten steel in the LF process for the purpose of raising the temperature, and it can be seen that the increased oxygen amount affects the wire rod product.

따라서, 전로에서 출강 시부터 고온을 목표로 하여 출강한 후, LF 공정에서 전극봉을 통한 승온 시간을 최소화함으로써 용강 내 개재물 품질을 개선하고, 내구성 및 내마모성이 우수한 베어링강 선재를 제조할 수 있다.
Therefore, after tapping at a high temperature from the tapping in the converter, by minimizing the temperature rise time through the electrode in the LF process, it is possible to improve the quality of inclusions in the molten steel, and to produce a bearing steel wire with excellent durability and wear resistance.

Claims (2)

전로에서, 중량%로, C: 0.9?1.4%, Si: 0.15?0.25%, Mn: 0.25?0.45%, Cr: 1.3?1.6%, P: 0.02%이하, S: 0.008%이하, 나머지 Fe 및 기타 불가피한 불순물로 조성된 용강을 제조한 후, 1630?1680℃의 온도에서 출강하고, LF 설비에서 승온시간을 10?19분으로 하여 LF처리를 행하고, 25?35분의 용강환류시간 조건으로 RH 공정을 행한 후, 주조한 다음, 강편압연하고, 선재압연하는 내구성 및 내마모성이 우수한 베어링 강 선재의 제조방법.In the converter, in weight%, C: 0.9 to 1.4%, Si: 0.15 to 0.25%, Mn: 0.25 to 0.45%, Cr: 1.3 to 1.6%, P: 0.02% or less, S: 0.008% or less, remaining Fe and After manufacturing molten steel composed of other unavoidable impurities, tapping is performed at a temperature of 1630-1680 ° C., LF treatment is performed at a temperature raising time of 10 to 19 minutes in an LF facility, and RH is subjected to a molten steel reflux time of 25 to 35 minutes. A method for producing a bearing steel wire which is excellent in durability and wear resistance after steel-rolling and wire rod rolling after casting. 제1항에 있어서, 상기 선재의 T[O]값(총 산소량)은 5ppm 이하인 것을 특징으로 하는 내구성 및 내마모성이 우수한 베어링 강 선재의 제조방법.



The method for producing bearing steel wire having excellent durability and wear resistance according to claim 1, wherein the T [O] value (total amount of oxygen) of the wire is 5 ppm or less.



KR1020100133188A 2010-12-23 2010-12-23 Method for Manufacturing Bearing Steel Wire Rod Having Excellent Durability and Abrasion Resistance KR101242987B1 (en)

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