KR100398378B1 - The method of manufacturing wire rods for the stabilizer of automobile - Google Patents

The method of manufacturing wire rods for the stabilizer of automobile Download PDF

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Publication number
KR100398378B1
KR100398378B1 KR10-1998-0042859A KR19980042859A KR100398378B1 KR 100398378 B1 KR100398378 B1 KR 100398378B1 KR 19980042859 A KR19980042859 A KR 19980042859A KR 100398378 B1 KR100398378 B1 KR 100398378B1
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stabilizer
wire
automobile
steel
present
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KR10-1998-0042859A
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Korean (ko)
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KR20000025695A (en
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신병현
안근식
한승규
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주식회사 포스코
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    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

본 발명은 자동차 스테빌라이저용 선재의 제조방법에 관한 것이며, 그 목적은, 소입·소려열처리공정의 생략이 가능하면서도 보다 피로특성이 개선되는 스테빌라이저용 비조질강선재의 제조방법을 제공하는 것으로, 본 발명에 따라 제공되는 선재는 피로특성이 요구되는 각종 재료에 적용될 수 있다.The present invention relates to a method for producing a wire rod for automobile stabilizers, and an object thereof is to provide a method for manufacturing a non-coarse steel wire for stabilizer, which can eliminate the hardening and annealing heat treatment process and improves fatigue characteristics. The wire rod provided in accordance with the invention can be applied to various materials requiring fatigue properties.

이와 같은 목적을 갖는 본 발명은,The present invention having such an object,

중량%로, C:0.35-0.55%, Si:0.50-0.70%, Mn:1.0-1.3%, P:0.030%이하, S:0.030%이하, Al:0.01-0.050%, V:0.10-0.15%, Ti:0.01-0.03%, Cr:0.05-0.20%, N:0.005-0.015%와 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성되는 강편을 900-1200℃로 가열하여 열간선재압연한 다음 750-950℃의 온도범위에서 권취하고 이어 300-600℃의 온도구간을 0.5-20℃/sec의 속도로 냉각하는 것을 포함하여 구성되는 피로특성이 우수한 자동차 스테빌라이저용 비조질강 선재의 제조방법에 관한 것을 그 기술적요지로 한다.By weight%, C: 0.35-0.55%, Si: 0.50-0.70%, Mn: 1.0-1.3%, P: 0.030% or less, S: 0.030% or less, Al: 0.01-0.050%, V: 0.10-0.15% , Steel sheet consisting of Ti: 0.01-0.03%, Cr: 0.05-0.20%, N: 0.005-0.015% and the remaining Fe and other unavoidable impurities, were heated to 900-1200 ° C., followed by hot wire rolling. The present invention relates to a method for producing an amorphous steel wire for automobile stabilizers having excellent fatigue characteristics, including winding in a temperature range of 950 ° C. and then cooling the temperature section of 300-600 ° C. at a rate of 0.5-20 ° C./sec. It is to the technical point.

Description

피로특성이 우수한 자동차 스테빌라이저용 비조질강 선재의 제조방법{THE METHOD OF MANUFACTURING WIRE RODS FOR THE STABILIZER OF AUTOMOBILE}Manufacturing method of non-steel steel wire for automobile stabilizer with excellent fatigue characteristics {THE METHOD OF MANUFACTURING WIRE RODS FOR THE STABILIZER OF AUTOMOBILE}

본 발명은 자동차 스테빌라이저용 선재의 제조방법에 관한 것으로, 보다 상세히는 소입-소려열처리를 생략한 비조질강 선재의 제조방법에 속한다.BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing wire rods for automobile stabilizers, and more particularly, to a method for producing non-coarse steel wire rods without quenching-treating heat treatment.

일반적으로 자동차 스테빌라이저는 차량의 주행회전시 차체의 안정성을 유지하는 현가장치의 일종으로, 일정량 이상의 강도와 반복하중을 견딜 수 있는 높은 피로수명의 재질특성을 필요로 한다. 이러한 스테빌라이저의 재질특성을 만족시키기 위해 지금까지는 아래 표 1과 같이 조성되는 선재를 사용하고 있었다.In general, the automobile stabilizer is a kind of suspension device that maintains the stability of the vehicle body when the vehicle rotates, and requires a material property of high fatigue life that can withstand a certain amount of strength and repeated load. In order to satisfy the material properties of these stabilizers, wire rods are used so far as shown in Table 1 below.

강종Steel grade 화학조성(중량%)Chemical composition (% by weight) CC SiSi MnMn PP SS 0.56-0.640.56-0.64 1.80-2.201.80-2.20 0.70-1.00.70-1.0 0.035이하Less than 0.035 0.035이하Less than 0.035

위와 같이 조성되는 선재는 도 1(a)에 도시된 바와 같이, 표면결함 및 탈탄층을 제거하기 위해 표면을 깎아내는 필링(peeling)공정을 거쳐 원하는 치수의 필링바(peeling bar)를 제조하고, 이 필링바를 열간가공 공정을 거쳐 원하는 형상으로 제조(스테빌라이저)하고 최종제품에서 요구되는 강도와 인성을 확보하기 위해 소입과 소려 열처리를 실시한다. 이어 스테빌라이저 표면에 지름이 약 0.5-1.5mm 가량의 금속구를 충돌시켜 표면 압축잔류응력을 부여하고 이러한 압축잔류응력에 의해 피로수명을 향상시키는 숏피닝 공정을 거치고 교정과 도금공정을 거쳐 최종제품으로 된다.As shown in FIG. 1 (a), the wire rod formed as above is manufactured with a peeling bar having a desired dimension through a peeling process to remove the surface defects and the decarburized layer. The peeling bar is manufactured into a desired shape through a hot working process (stabilizer) and subjected to hardening and annealing heat treatment to secure the strength and toughness required for the final product. Then, the surface of the stabilizer is hit by a metal ball of about 0.5-1.5mm in diameter to impart a surface compressive residual stress, and after the shot peening process to improve the fatigue life by the compressed residual stress, the final product undergoes calibration and plating process. Becomes

상기 열처리공정(소입, 소려열처리)은 열간성형된 스테빌라이저용 바(bar)를 900℃이상 가열한 후 30-70℃의 오일욕조에 급냉시키는 소입열처리를 한다. 소입처리된 스테빌라이저용 바는 마르텐사이트 조직으로 내피로 수명에 취약한 조직이므로 다시 400-520℃로에서 60분 가량 소려열처리 실시하게 된다. 이와 같이 하여 제조된 스테빌라이저용 바는 소르바이트(Sorbite)조직으로 변태하게 되어 고강도와 고인성의 특성을 갖는다. 그러나, 소입·소려열처리공정의 채택으로 제조공정이 복잡하고 제조단가가 비싸다는 문제가 있다.The heat treatment process (hardening, sour heat treatment) is subjected to a hardening heat treatment to heat the hot-formed stabilizer bar (900) more than 900 ℃ and quench in an oil bath of 30-70 ℃. The quenched stabilizer bar is martensitic and vulnerable to endothelial life, so it is subjected to heat treatment for about 60 minutes at 400-520 ℃. The stabilizer bar manufactured in this manner is transformed into a sorbite (Sorbite) structure has high strength and high toughness. However, there is a problem that the manufacturing process is complicated and the manufacturing cost is expensive due to the adoption of the hardening and heat treatment process.

본 발명은 상기한 종래문제를 개선하기 위해 안출된 것으로서, 소입·소려열처리공정의 생략이 가능하면서도 보다 피로특성이 개선되는 스테빌라이저용 비조질강선재의 제조방법을 제공하는데, 그 목적이 있다.SUMMARY OF THE INVENTION The present invention has been made to improve the above-mentioned conventional problems, and provides a method for manufacturing a non-coarse steel wire for stabilizer, which can eliminate the hardening and annealing heat treatment process and improves fatigue characteristics.

도 1은 스테빌라이저의 제조공정도로서1 is a manufacturing process diagram of a stabilizer

도 1(a)는 종래의 공정도Figure 1 (a) is a conventional process diagram

도 1(b)는 본 발명의 공정도Figure 1 (b) is a process diagram of the present invention

상기 목적을 달성하기 위한 본 발명의 비조질강 선재의 제조방법은, 중량%로, C:0.35-0.55%, Si:0.50-0.70%, Mn:1.0-1.3%, P:0.030%이하, S:0.030%이하, Al:0.01-0.050%, V:0.10-0.15%, Ti:0.01-0.03%, Cr:0.05-0.20%, N:0.005-0.015%와 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성되는 강편을 900-1200℃로 가열하여 열간선재압연한 다음, 750-950℃의 온도범위에서 권취하고 이어 300-600℃의 온도구간을 0.5-20℃/sec의 속도로 냉각하는 것을 포함하여 구성된다.In order to achieve the above object, the manufacturing method of the non-coated steel wire of the present invention, in weight%, C: 0.35-0.55%, Si: 0.50-0.70%, Mn: 1.0-1.3%, P: 0.030% or less, S: 0.030% or less, Al: 0.01-0.050%, V: 0.10-0.15%, Ti: 0.01-0.03%, Cr: 0.05-0.20%, N: 0.005-0.015% and the remaining Fe and other inevitable impurities The steel sheet is heated to 900-1200 ° C. to be hot rolled, and then wound in a temperature range of 750-950 ° C., followed by cooling the temperature section of 300-600 ° C. at a rate of 0.5-20 ° C./sec. do.

이하, 본 발명을 설명한다.Hereinafter, the present invention will be described.

본 발명은 소입·소려열처리를 생략하고도 원하는 목표재질을 확보하고 나아가 피로특성이 보다 개선되는 스테빌라이저용 선재를 제공하는데, 이는The present invention provides a stabilizer wire rod that ensures a desired target material and further improves fatigue characteristics without omitting quenching and heat treatment.

1) Mn, Si성분 첨가에 의한 고용강화와1) solid solution strengthening by adding Mn and Si

2) V, Cr, Ti등의 미량합금원소에 의한 석출경화로 비열처리에 따른 강의 강도를 보상하고,2) Compensation for the strength of steel due to specific heat treatment by precipitation hardening by trace alloy elements such as V, Cr, Ti, etc.

3) S 및 Al을 포함한 기타성분을 적절히 관리하여 피로특성을 개선하면서, 이에 맞추어 제조조건을 적절히 설정하는 것에 의해 달성된다. 이를 강성분계와 제조조건을 통해 상세히 설명한다.3) Achievement is achieved by appropriately managing other components including S and Al to improve the fatigue properties, while setting the manufacturing conditions appropriately. This will be described in detail through a steel component system and manufacturing conditions.

우선, 상기 탄소(C)는 소재의 강도를 결정짓는 주요원소로 탄소함량이 0.35%이하 첨가시 강도를 얻을 수 없으며, 0.55%이상 첨가시 중심부 편석대의 발생 및 그로 인해 냉각시 저온변태조직인 마르텐사이트, 베이나이트조직이 발생할 수 있으므로, 탄소는 0.35-0.55%로 제한하는 것이 바람직하다.First, the carbon (C) is a major element that determines the strength of the material, the carbon content can not be obtained when the carbon content is added below 0.35%, the addition of more than 0.55% of the segregation of the central zone and thereby the marten, a low temperature transformation structure during cooling Since the site and bainite structure may occur, the carbon is preferably limited to 0.35-0.55%.

규소(Si)는 페라이트 고용강화에 의한 강도향상을 위해 0.50%이상 첨가하나 0.70%이상 첨가되는 경우 표면탈탄이 과다하게 발생하므로 0.50-0.70%로 첨가한다.Silicon (Si) is added at 0.50% or more to improve the strength by strengthening the ferrite solid solution, but when it is added at 0.70% or more, the surface decarburization occurs excessively, so it is added at 0.50-0.70%.

망간(Mn)은 고용강화에 의한 선재상태에서의 강도확보를 위해 1.0%이상 첨가하나, 1.3%이상 첨가시 중심부 Mn편석에 의한 마르텐사이트, 베이나이트조직이 발생할 수 있으므로 1.0-1.3%의 범위로 첨가한다.Manganese (Mn) is added in an amount of 1.0% or more to secure the strength of wire rod by solid solution strengthening, but when it is added more than 1.3%, martensite and bainite structure may occur due to segregation of central Mn. Add.

인(P) 및 황(S)은 각각 인에 의한 인성저하와 MnS계 비금속개재물 증가로 인한 스테빌라이저의 피로특성의 저하를 막기 위해 0.030%이하로 첨가한다.Phosphorus (P) and sulfur (S) are added below 0.030% in order to prevent the degradation of the fatigue properties of the stabilizer due to the decrease in toughness caused by phosphorus and the increase of MnS-based nonmetallic inclusions.

알루미늄(Al)은 0.010-0.050%의 범위로 첨가하는데, 이는 0.010%이하로 첨가시 탈산부족으로 선재에 흠이 생길 수 있으며, 0.05%이상으로 첨가하는 경우 도리어 알루미늄 비금속 개재물에 의한 피로특성이 저하될 수 있기 때문이다.Aluminum (Al) is added in the range of 0.010-0.050%, which may cause defects in the wire rod due to the lack of deoxidation when added below 0.010%, and when added at 0.05% or more, fatigue characteristics due to aluminum non-metallic inclusions decrease. Because it can be.

바나듐(V), 티타늄(Ti) 및 질소(N)는 각각 0.10-0.15%, 0.010-0.030%, 0.005-0.015%로 첨가하는데, 이는 바나듐, 티타늄 등이 질소와 질소화합물을 만들어 페라이트내로 석출하여 석출경화에 의한 목표강도를 얻을 수 있는 최적의 첨가량이기 때문이다.Vanadium (V), titanium (Ti), and nitrogen (N) are added at 0.10-0.15%, 0.010-0.030%, and 0.005-0.015%, respectively. This is because the optimum addition amount can obtain the target strength by precipitation hardening.

크롬(Cr)은 탄소와 결합하여 크롬탄화물에 의한 강도향상 목적으로 0.05%이상 첨가하나 0.20%를 넘는 경우 강도가 너무 높아지고 소재의 가격이 비싸지므로 첨가범위를 0.05-0.20%로 제한하는 것이 바람직하다.Chromium (Cr) is combined with carbon to add more than 0.05% for the purpose of strength improvement by chromium carbide, but if it exceeds 0.20%, the strength is too high and the price of the material is expensive, so it is desirable to limit the addition range to 0.05-0.20%. .

상기와 같은 조성되는 강을 재가열하여 열간선재압연 하는데, 이때의 재가열온도는 900-1200℃가 바람직하다. 그 이유는 재가열온도가 900℃이하의 경우 압연작업이 곤란하며, 1200℃를 넘으면 표면탈탄층이 증가하고 오스테나이트 입자성장에 의한 마르텐사이트 발생 가능성이 높기 때문이다.Reheating the steel composition as described above is hot wire re-rolling, the reheating temperature is preferably 900-1200 ℃. The reason is that when the reheating temperature is below 900 ° C., the rolling operation is difficult, and when it exceeds 1200 ° C., the surface decarburization layer increases and the martensite generation due to austenite grain growth is high.

상기와 같이 재가열한 후 열간선재압연하고 코일형태로 권취하는데, 이때의 권취온도는 750-950℃가 바람직하다. 이는 권취온도가 750℃이하의 경우 권취작업이 곤란하며 950℃이상의 경우 오스테나이트 성장 및 선재냉각조절의 어려움 등으로 목표재질인 페라이트와 펄라이트 조직을 얻을 수 없기 때문이다.After reheating as described above, the hot wire is rolled and wound in a coil form. At this time, the coiling temperature is preferably 750-950 ° C. This is because the winding operation is difficult when the winding temperature is less than 750 ℃ and the target material of ferrite and pearlite can not be obtained in the above 950 ℃ due to the difficulty of austenite growth and wire cooling control.

상기와 같이 권취한 선재는 상변태구간(300-600℃)을 0.5-20℃/sec의 냉각속도로 냉각시키는 것이 바람직하다. 냉각속도가 0.5℃/sec이하의 경우 석출물에 의한 강도확보를 얻을 수 없으며, 20℃/sec이상 냉각시 마르텐사이트, 베이나이트 등의 유해조직이 발생하기 때문이다.The wire wound as described above is preferably cooled to the phase transformation section (300-600 ℃) at a cooling rate of 0.5-20 ℃ / sec. If the cooling rate is 0.5 ℃ / sec or less can not be obtained by the strength of the precipitate, because when cooling 20 ℃ / sec or more harmful structures such as martensite, bainite occurs.

이와 같이 제조된 선재는 종래재와 동등수준이상의 재질특성을 보이며, 소입·소려 열처리를 생략한 최종제품에서도 종래의 스프링강재와 동등 이상의 피로특성을 갖는 자동차 스테빌라이저용 바의 특성을 갖는다.The wire rod manufactured as described above exhibits material properties equal to or higher than those of conventional materials, and has the characteristics of automobile stabilizer bars having fatigue properties equivalent to or higher than those of conventional spring steel even in the final product omitting quenching and annealing.

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

[실시예 1]Example 1

본 발명의 실시예에 적용된 발명강 및 종래강의 화학성분은 아래 표 2와 같다.Chemical compositions of the inventive steel and conventional steel applied to the embodiment of the present invention are shown in Table 2 below.

구분division 화학조성(중량%,N:ppm)Chemical composition (% by weight, N: ppm) CC SiSi MnMn PP SS AlAl VV TiTi CrCr NN 발명강Invention steel 1One 0.450.45 0.600.60 1.201.20 0.0120.012 0.0100.010 0.0350.035 0.100.10 0.0200.020 0.100.10 105105 22 0.450.45 0.700.70 1.301.30 0.0100.010 0.0100.010 0.0300.030 0.090.09 0.0200.020 0.100.10 100100 33 0.430.43 0.500.50 1.201.20 0.0150.015 0.0100.010 0.0310.031 0.100.10 0.0210.021 0.110.11 9595 종래강Conventional Steel 0.600.60 2.02.0 0.850.85 0.0120.012 0.0100.010 0.0350.035

표 2와 같이 조성되는 강 성분계를 전로에서 제강한 다음 진공탈개스설비를 이용하여 유해가스를 제거하였는데 이때의 진공도는 2.0torr이하이고, 처리시간은 22분동안하였다. 탈가스처리를 마친 용강을 연주설비에 용강의 이론응고에 20℃이하로 관리하고 0.6-0.9m/min의 속도로 주조한 부룸(bloom, 250×330mm)을 재가열한 후 단면이 160×160mm인 빌렛(billet)으로 강편압연을 하였다.The steel component system, as shown in Table 2, was removed from the converter and the harmful gas was removed using a vacuum degassing facility. The vacuum degree was 2.0 torr or less and the treatment time was 22 minutes. After degassing, the molten steel is managed below 20 ℃ for theoretical coagulation of molten steel in reheating equipment, and after reheating the blown (250 × 330mm) at 0.6-0.9m / min, the cross section is 160 × 160mm. Steel sheet rolling was performed by billet.

상기 강편을 아래 표 3의 조건으로 제조한 다음 선재 및 스테빌라이저의 재질을 평가하고 그 결과를 아래 표 4 및 5에 나타내었다.The steel sheet was manufactured under the conditions of Table 3 below, and the materials of the wire rod and the stabilizer were evaluated, and the results are shown in Tables 4 and 5 below.

구분division 재가열Reheat 권취온도(℃)Winding temperature (℃) 평균냉각속도(℃/sec)Average cooling rate (℃ / sec) 온도(℃)Temperature (℃) 시간(min)Time (min) 발명재Invention 1One 10001000 9393 830830 1515 22 10101010 9898 780780 2020 33 10301030 100100 785785 2020 종래재Conventional 10301030 9292 780780 88

구분division 기계적성질Mechanical property 최대전탈탄(mm)Total decarburization (mm) 청정도(%)cleanliness(%) 인장강도(kg/mm2)Tensile Strength (kg / mm 2 ) 단면감소율(RA)(%)Cross Section Reduction (RA) (%) 경도(HRc)Hardness (HRc) 발명재Invention 1One 93.493.4 4545 2727 0.100.10 0.0350.035 22 98.198.1 4242 3030 0.120.12 0.0370.037 33 9595 4646 2929 0.080.08 0.0300.030 종래재Conventional 95.095.0 5555 2828 0.210.21 0.0250.025

위의 표 3에 나타난 바와 같이, 본 발명에 따라 제조한 선재는 종래재와 동등이상의 재질특성을 가짐을 알 수 있다.As shown in Table 3 above, it can be seen that the wire rod prepared according to the present invention has a material characteristic equivalent to that of the conventional material.

구분division 현미경조직Tissue 응력기준(kg/mm2)Stress standard (kg / mm 2 ) 피로수명 시험결과Fatigue Life Test Results 피로수명기준Fatigue Life Criteria 발명재Invention 1One 페라이트+펄라이트Ferrite + Pearlite 20-6020-60 53만회530,000 times 30만회 이상300,000 times or more 22 "" 56만회560,000 times "" 33 "" 49만회490,000 times "" 종래재* Conventional material * 소르바이트Sorbite "" 45만회450,000 times 30만회 이상300,000 times or more *종래재는 선재를 소입,소려 열처리 한 것임.* Conventional materials are hardened and heat treated wires.

위의 표 5에 나타난 바와 같이, 소입·소려열처리를 생략하여 제조한 본 발명의 스테빌라이저의 피로수명값은 종래재의 소입, 소려의 열처리를 실시한 스프링강재와 유사한 50만회이상의 우수한 피로특성값을 얻을 수 있었다.As shown in Table 5 above, the fatigue life value of the stabilizer of the present invention manufactured by omitting the quenching and annealing heat treatment can obtain an excellent fatigue characteristic value of 500,000 times or more similar to that of the spring steel subjected to the quenching and heat treatment of conventional materials. Could.

상술한 바와 같이, 본 발명에 의하면 소입·소려열처리를 생략한 비조질강선재를 제공할 수 있으며, 이 선재는 높은 피로특성을 가지고 있어 이러한 특성이 요구되는 각종 소재로 이용될 수 있으며 특히, 자동차 스테빌라이저 등에 유용하게 적용될 수 있다.As described above, according to the present invention, it is possible to provide an amorphous steel wire which eliminates quenching and heat treatment, and this wire has a high fatigue characteristic, so that it can be used in various materials requiring such characteristics, in particular, automobile stabilization. It can be usefully applied to a riser.

Claims (1)

중량%로, C:0.35-0.55%, Si:0.50-0.70%, Mn:1.0-1.3%, P:0.030%이하, S:0.030%이하, Al:0.01-0.050%, V:0.10-0.15%, Ti:0.01-0.03%, Cr:0.05-0.20%, N:0.005-0.015%와 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성되는 강편을 900-1200℃로 가열하여 열간선재압연한 다음, 750-950℃의 온도범위에서 권취하고 이어 300-600℃의 온도구간을 0.5-20℃/sec의 속도로 냉각하는 것을 포함하여 구성되는 피로특성이 우수한 자동차 스테빌라이저용 비조질강 선재의 제조방법.By weight%, C: 0.35-0.55%, Si: 0.50-0.70%, Mn: 1.0-1.3%, P: 0.030% or less, S: 0.030% or less, Al: 0.01-0.050%, V: 0.10-0.15% , The steel: Ti: 0.01-0.03%, Cr: 0.05-0.20%, N: 0.005-0.015% and the remaining Fe and other inevitably contained impurities are heated to 900-1200 ℃ hot-rolled wire rod, then 750 A method for producing an amorphous steel wire for automobile stabilizers having excellent fatigue characteristics, including winding in a temperature range of -950 ° C and then cooling a temperature section of 300-600 ° C at a rate of 0.5-20 ° C / sec.
KR10-1998-0042859A 1998-10-13 1998-10-13 The method of manufacturing wire rods for the stabilizer of automobile KR100398378B1 (en)

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KR101461763B1 (en) 2012-12-27 2014-11-13 주식회사 포스코 Non-quenched and tempered steel wire rod having excellent toughness and manufacturing method thereof

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KR20240048780A (en) 2022-10-07 2024-04-16 심수연 A Platform for Recommending Fairy Tale Books using AI Algorithm based on the 5W1H

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JPH0432514A (en) * 1990-05-30 1992-02-04 Nippon Steel Corp Production of soft wire rod free from surface abnormal phase in as-rolled state
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JPS59123741A (en) * 1982-12-28 1984-07-17 Kobe Steel Ltd Hot-rolled high-tension wire rod requiring no heat treatment
JPH0432514A (en) * 1990-05-30 1992-02-04 Nippon Steel Corp Production of soft wire rod free from surface abnormal phase in as-rolled state
KR19980045319A (en) * 1996-12-10 1998-09-15 김종진 Manufacturing method of high carbon steel with excellent cold rolled workability
JP2000017390A (en) * 1998-06-30 2000-01-18 Toa Steel Co Ltd High strength cold forming non-heat treated steel material for shock-absorbing/restoring mechanism member
KR20000007446A (en) * 1998-07-03 2000-02-07 이구택 Process for preparing high-carbon steel rod wire

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KR101461763B1 (en) 2012-12-27 2014-11-13 주식회사 포스코 Non-quenched and tempered steel wire rod having excellent toughness and manufacturing method thereof

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