KR101165654B1 - Abrasion-resistant steel sheet having excellent processability, and method for production thereof - Google Patents

Abrasion-resistant steel sheet having excellent processability, and method for production thereof Download PDF

Info

Publication number
KR101165654B1
KR101165654B1 KR1020097021902A KR20097021902A KR101165654B1 KR 101165654 B1 KR101165654 B1 KR 101165654B1 KR 1020097021902 A KR1020097021902 A KR 1020097021902A KR 20097021902 A KR20097021902 A KR 20097021902A KR 101165654 B1 KR101165654 B1 KR 101165654B1
Authority
KR
South Korea
Prior art keywords
wear
less
resistant steel
phase
steel sheet
Prior art date
Application number
KR1020097021902A
Other languages
Korean (ko)
Other versions
KR20090123006A (en
Inventor
야스히로 무로타
미사오 이시카와
요시노리 와타나베
신이치 스즈키
노부오 시카나이
Original Assignee
제이에프이 스틸 가부시키가이샤
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 제이에프이 스틸 가부시키가이샤 filed Critical 제이에프이 스틸 가부시키가이샤
Publication of KR20090123006A publication Critical patent/KR20090123006A/en
Application granted granted Critical
Publication of KR101165654B1 publication Critical patent/KR101165654B1/en

Links

Images

Classifications

    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Landscapes

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

Abstract

파워 셔블 등 토사와 접촉하는 부재용으로서 적합하고, 굽힘 가공성이 우수한 내마모 강판 및 그 제조 방법을 제공한다. 구체적으로는, 질량％ 로, C : 0.05 ～ 0.35 ％, Si : 0.05 ～ 1.0 ％, Mn : 0.1 ～ 2.0 ％, Ti : 0.1 ～ 1.2 ％, Al : 0.1 ％ 이하, 추가로 Cu : 0.1 ～ 1.0 ％, Ni : 0.1 ～ 2.0 ％, Cr : 0.1 ～ 1.0 ％, Mo : 0.05 ～ 1.0 ％, W : 0.05 ～ 1.0 ％, B : 0.0003 ～ 0.0030 ％ 의 1 종 또는 2 종 이상을 함유하고, 하기 식으로 나타내는 DI* 가 60 미만이고, 또한 필요에 따라, Nb : 0.005 ～ 1.0 ％, V : 0.005 ～ 1.0 ％ 의 1 종 또는 2 종, 잔부 Fe 및 불가피적 불순물로 이루어지는 강판. DI* ＝ 33.85 × (0.1 × C*)0.5 × (0.7 × Si ＋ 1) × (3.33 × Mn ＋ 1) × (0.35 × Cu ＋ 1) × (0.36 × Ni ＋ 1) × (2.16 × Cr ＋ 1) × (3 × Mo* ＋ 1) × (1.5 × W* ＋ 1) (1) 단, C* ＝ C － 1/4 × (Ti － 48/14N), Mo* ＝ Mo × (1 － 0.5 × (Ti － 48/14N)), W* ＝ W × (1 － 0.5 × (Ti － 48/14N))Provided is a wear resistant steel sheet suitable for a member in contact with soil sand, such as a power shovel, and excellent in bending workability, and a manufacturing method thereof. Specifically, in mass%, C: 0.05 to 0.35%, Si: 0.05 to 1.0%, Mn: 0.1 to 2.0%, Ti: 0.1 to 1.2%, Al: 0.1% or less, and further Cu: 0.1 to 1.0% , Ni: 0.1% to 2.0%, Cr: 0.1% to 1.0%, Mo: 0.05% to 1.0%, W: 0.05% to 1.0%, B: 0.0003% to 0.0030%. DI * is less than 60, and if necessary, Nb: 0.005 to 1.0%, V: 0.005 to 1.0% of 1 or 2 types, remainder Fe and an unavoidable impurity steel plate. DI * = 33.85 × (0.1 × C *) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo * + 1) × (1.5 × W * + 1) (1) However, C * = C-1/4 × (Ti-48 / 14N), Mo * = Mo × (1- 0.5 × (Ti-48 / 14N)), W * = W × (1-0.5 × (Ti-48 / 14N))

Description

가공성이 우수한 내마모 강판 및 그 제조 방법{ABRASION-RESISTANT STEEL SHEET HAVING EXCELLENT PROCESSABILITY, AND METHOD FOR PRODUCTION THEREOF}Abrasion resistant steel sheet excellent in workability and its manufacturing method {ABRASION-RESISTANT STEEL SHEET HAVING EXCELLENT PROCESSABILITY, AND METHOD FOR PRODUCTION THEREOF}

본 발명은, 건설 (construction), 토목 (civil engineering), 광산 (mining) 등의 분야에서 사용되는, 예를 들어, 파워 셔블 (power shovels), 불도저 (bulldozers), 호퍼 (hoppers), 버킷 (buckets) 등의 산업 기계 (industrial machine) 나 운반 기기 (transporting machine) 등에서, 토사 (earth and sand) 와의 접촉에 의한 마모 (wear or abrasion) 가 문제가 되는 부재용으로서 적합한 내마모 강판 (abrasion resistant steel) 및 그 제조 방법에 관한 것으로, 특히 굽힘 가공성 (bending formability) 이 우수한 것에 관한 것이다.The invention is used in the fields of construction, civil engineering, mining, etc., for example, power shovels, bulldozers, hoppers, buckets (Abrasion resistant steel) suitable for use in parts such as wear or abrasion caused by contact with earth and sand in industrial machines or transporting machines. And to a method for producing the same, and more particularly, to excellent bending formability.

흙, 모래 등에 의한 마모를 받는 부재에는, 장수명화를 위해 내마모성이 우수한 강재가 사용된다. 강재의 내마모성 (abrasion resistant property) 은, 고경도화함으로써 향상되는 것이 알려져, 내마모성이 요구되는 부재에는, Cr, Mo 등의 합금 원소를 대량으로 첨가한 강재에 담금질 등의 열처리를 실시하여 고경도화된 강재가 사용되어 왔다.In a member subjected to abrasion by soil, sand, or the like, steel materials excellent in wear resistance are used for long service life. It is known that the abrasion resistant property of steel is improved by making it hard, and the hardened steel is heat-treated by hardening, such as quenching, on the steel which added a large amount of alloying elements, such as Cr and Mo, to the member which requires abrasion resistance Has been used.

예를 들어, 일본 공개특허공보 소62-142726호에는, C : 0.10 ～ 0.19 ％ 를 함유하고, Si, Mn 을 적정량 함유하고, Ceq 를 0.35 ～ 0.44 ％ 로 한정한 강을, 열간 압연 후 직접 담금질하거나, 또는 900 ～ 950 ℃ 로 재가열한 후 담금질하고, 300 ～ 500 ℃ 에서 템퍼링하여, 강판 표면 경도를 300 HV (Vickers hardness) 이상으로 하는 내마모 강판의 제조 방법이 제안되어 있다.For example, Japanese Patent Laid-Open No. 62-142726 directly quenchs a steel containing C: 0.10% to 0.19%, an appropriate amount of Si and Mn, and limited Ceq to 0.35% to 0.44% after hot rolling. Alternatively, there has been proposed a method for producing a wear resistant steel sheet which is quenched after reheating at 900 to 950 ° C., tempered at 300 to 500 ° C., and having a steel sheet surface hardness of 300 HV (Vickers hardness) or more.

일본 공개특허공보 소63-169359호에는, C : 0.10 ～ 0.20 ％ 를 함유하고, Si, Mn, P, S, N, Al 을 적정량으로 조정하거나, 또는 추가로 Cu, Ni, Cr, Mo, B 의 1 종 이상을 함유하는 강에, 열간 압연 후 직접 담금질하거나, 또는 압연 후 방랭시킨 후, 재가열하고 담금질하여, 340 HB (Brinell hardness) 이상의 경도를 부여하는 내마모 후강판의 제조 방법이 제안되어 있다.Japanese Laid-Open Patent Publication No. 63-169359 contains C: 0.10% to 0.20% and adjusts Si, Mn, P, S, N, Al to an appropriate amount, or further Cu, Ni, Cr, Mo, B A method for producing a wear-resistant thick steel sheet which is quenched directly in a steel containing at least one of the following or after quenching after hot rolling, or after cooling, is reheated and quenched to impart a hardness of 340 HB (Brinell hardness) or more. have.

일본 공개특허공보 평1-142023호에는, C : 0.07 ～ 0.17 ％ 를 함유하고, Si, Mn, P, S, N, Al 을 적정량으로 조정하거나, 또는 추가로 Cu, Ni, Cr, Mo, B 의 1 종 이상을 함유하는 강에, 열간 압연 후 바로 담금질하거나, 또는 일단 실온까지 공랭시킨 후에 재가열하고 담금질하여, 표면 경도가 321 HB 이상이고, 굽힘 가공성이 우수한 강판으로 하는 내마모 강판의 제조 방법이 제안되어 있다.Unexamined-Japanese-Patent No. 1-142023 contains C: 0.07 to 0.17%, adjusts Si, Mn, P, S, N, Al to an appropriate amount, or further Cu, Ni, Cr, Mo, B A method for producing a wear-resistant steel sheet, which is quenched immediately after hot rolling in steel containing one or more kinds of steel, or is reheated and quenched after being cooled to room temperature once, to a steel sheet having a surface hardness of 321 HB or more and excellent bending workability. Is proposed.

일본 공개특허공보 소62-142726호, 일본 공개특허공보 소63-169359호 및 일본 공개특허공보 평1-142023호에 기재된 기술은, 합금 원소를 다량으로 첨가하고, 고용 경화 (solid solution hardening), 변태 경화 (transformation hardening), 석출 경화 (precipitation hardening) 등을 활용하여 고경도화함으로써, 내마모 특성을 향상시켰다. 그러나, 합금 원소를 다량으로 첨가하고, 고용 경화, 변태 경화, 석출 경화 등을 활용하여 고경도화한 경우에는, 용접성 (weldability), 가공성 (formability) 이 저하되게 되어, 더욱 제조 비용이 비싸진다.The techniques described in Japanese Patent Laid-Open No. 62-142726, Japanese Patent Laid-Open No. 63-169359, and Japanese Patent Laid-Open No. Hei 1-42023 add a large amount of alloying elements, solid solution hardening, Wear resistance was improved by high hardness using transformation hardening and precipitation hardening. However, when a large amount of alloying elements are added and high hardness is employed utilizing solid solution hardening, transformation hardening, precipitation hardening, or the like, weldability and formability are lowered, and manufacturing costs are more expensive.

그런데, 내마모성이 요구되는 부재의 경우, 사용 조건에 따라서는, 표면 및 표면 근방만을 고경도화하여 내마모성을 향상시키기만 해도 되는 경우가 있어, 이와 같은 경우에 사용되는 강재는, Cr, Mo 등의 합금 원소를 다량으로 첨가할 필요는 없고, 담금질 처리 등의 열처리를 실시하여 표면 및 표면 근방만을 담금질 조직 (hardened structure) 으로 하는 것을 생각해 볼 수 있다.By the way, in the case of a member requiring wear resistance, depending on the conditions of use, only the surface and the vicinity of the surface may be hardened to improve the wear resistance, and the steel used in such a case may be an alloy such as Cr or Mo. It is not necessary to add a large amount of elements, and it is conceivable to form a hardened structure only of the surface and the surface by performing heat treatment such as quenching treatment.

그러나, 담금질 조직의 고경도화를 위해서는, 일반적으로 강재의 고용 C 량을 증가시킬 필요가 있는데, 고용 C 량의 증가는 용접성의 저하, 굽힘 가공성의 저하 등을 초래하고, 특히 굽힘 가공성의 저하는 부재로서 필요한 굽힘 가공이 제한되어 사용 조건이 한정된다.However, in order to increase the hardness of the quenched structure, it is generally necessary to increase the amount of solid solution C of the steel, and the increase of the amount of solid solution C causes a decrease in weldability, a decrease in bending formability, and in particular, a decrease in bending formability. As necessary bending is limited and the use conditions are limited.

이 때문에, 과도하게 고경도화를 도모하지 않고, 내마모 특성을 향상시킬 수 있는 내마모 강판이 요망되어, 일본 특허공보 제3089882호에는, C : 0.10 ～ 0.45 ％ 를 함유하고, Si, Mn, P, S, N 을 적정량으로 조정하고, 추가로 Ti : 0.10 ～ 1.0 ％ 함유하고, 평균 입경 0.5 ㎛ 이상의 TiC 석출물 또는 TiC 와 TiN, TiS 의 복합 석출물을 400 개/㎟ 이상 함유하고, Ti* 가 0.05 ％ 이상 0.4 ％ 미만으로 하는 표면 성상이 우수한 내마모 강이 제안되어 있다.For this reason, the wear-resistant steel plate which can improve abrasion resistance characteristics is not desired, but excessively hardening is calculated | required, Japanese Patent Publication No. 3089882 contains C: 0.10 to 0.45%, Si, Mn, P , S, N are adjusted to an appropriate amount, and Ti: 0.10 to 1.0% is further contained, and TiC precipitates having an average particle diameter of 0.5 µm or more or 400 or more mm2 / mm2 composite precipitates are contained, and Ti * is 0.05. Abrasion resistant steels having excellent surface properties of at least% and less than 0.4% have been proposed.

또한, 일본 공개특허공보 평4-41616호에는, C : 0.05 ～ 0.45 ％, Si : 0.1 ～ 1.0 ％, Mn : 0.1 ～ 1.0 ％, Ti : 0.05 ～ 1.5 ％ 를 함유하고, 표면 경도를 브리넬 경도 (Brinell hardness) 로 401 이하로 함으로써, 굽힘 가공성을 향상시킨 내마모 강판의 제조 방법이 제안되어 있다.Moreover, Unexamined-Japanese-Patent No. 4-41616 contains C: 0.05 to 0.45%, Si: 0.1 to 1.0%, Mn: 0.1 to 1.0%, Ti: 0.05 to 1.5%, and surface hardness is referred to as Brinell hardness ( The manufacturing method of the wear resistant steel plate which improved bending workability is proposed by setting it as 401 or less by Brinell hardness).

일본 특허공보 제3089882호, 일본 공개특허공보 평4-41616호에 기재된 기술 에 따르면, 응고시에 조대 (粗大) 한 TiC 를 주체로 하는 석출물을 생성시켜, 과도하게 고경도화시키지 않고 저렴하게 내마모성을 향상시킬 수 있다.According to the techniques described in Japanese Patent Publication No. 3089882 and Japanese Unexamined Patent Application Publication No. 4-41616, precipitates mainly composed of coarse TiC at the time of solidification are produced, and wear resistance is inexpensive without excessively high hardness. Can be improved.

그러나, 일본 특허공보 제3089882호에 기재된 기술에서는, 담금질 열처리를 실시하여, 조직을 담금질 상태의 마텐자이트 조직 (martensitic structure) 으로 하고 있기 때문에 강도가 높고, 그 결과, 굽힘 가공시의 변형 저항 (deformation resistance) 이 높아지기 때문에, 굽힘 가공이 용이하다고는 하기 어려워, 굽힘 가공성에 문제를 남겼다.However, in the technique described in Japanese Patent Publication No. 3089882, since the quenching heat treatment is performed to form the martensitic structure in the quenched state, the strength is high, and as a result, the deformation resistance during bending ( Since deformation resistance is high, it is difficult to say that bending processing is easy, and the problem remains in bending workability.

일본 공개특허공보 평4-41616호에 기재된 기술은, 굽힘 가공성을 확보하기 위해 표면 경도를 브리넬 경도로 401 이하로 규정하고 있는데, 합금 원소의 첨가량이 많기 때문에, 인장 강도는 780 ㎫ 를 초과하여, 가공시의 하중을 저감시키는 관점에서는 충분한 굽힘 가공성이 달성된 것은 아니다.In order to secure bending workability, the technique described in JP-A 4-41616 stipulates the surface hardness to be 401 or less in Brinell hardness, but the tensile strength exceeds 780 MPa because of the large amount of alloying elements added, In view of reducing the load during machining, sufficient bending formability has not been achieved.

또한, 일본 공개특허공보 소62-142726호, 일본 공개특허공보 소63-169359호, 일본 공개특허공보 평1-142023호, 일본 공개특허공보 평4-41616호 중 어느 것에 기재된 내마모 강이라도 열처리를 실시하는 것이 필수여서, 제조 공기 (工期), 제조 비용 (production cost) 면에서 과제를 남겼다.Moreover, even the wear-resistant steel of any of Unexamined-Japanese-Patent No. 62-142726, Unexamined-Japanese-Patent No. 63-169359, Unexamined-Japanese-Patent No. 1-42023, and Unexamined-Japanese-Patent No. 4-41616 is heat-processed. Since it is essential to implement, the problem remains in terms of production air and production cost.

그래서, 본 발명은, 열간 압연의 상태에서 열처리를 실시하지 않고 제조할 수 있고, 내마모성 및 굽힘 가공성이 우수한 내마모 강판 및 그 제조 방법을 제공하는 것을 목적으로 한다.Then, an object of this invention is to provide the wear resistant steel plate which can be manufactured without performing heat processing in the state of hot rolling, and is excellent in abrasion resistance and bending workability, and its manufacturing method.

발명의 개시DISCLOSURE OF INVENTION

발명자들은, 상기한 목적을 달성하기 위해, 내마모성과 굽힘 가공성에 영향을 주는 각종 요인에 대해 예의 연구를 거듭하여, Ti 와 C 를 함유하는 성분계를 갖고, 금속 조직 (microstructure of base metal) 이 압연 상태의 페라이트-펄라이트 조직 (ferrite and pearlite structure) 의 복합 조직 (complex structure) 을 기지상 (base phase) 으로 하고, 또한 매트릭스 (matrix) 중에 경질인 제 2 상 (second phase) (경질상 (hard phase) : Ti 계 탄화물) 을 분산시킴으로써, 내마모성을 확보한 상태에서 굽힘 가공시의 가공 하중 저감이 가능하며, 요컨대 굽힘 가공성의 개선이 가능한 것을 알아냈다.The inventors earnestly studied various factors affecting wear resistance and bending workability in order to achieve the above object, and have a component system containing Ti and C, and the microstructure of base metal is in a rolled state. The complex structure of the ferrite and pearlite structure of is made into the base phase, and also the second phase (hard phase) which is hard in the matrix: By dispersing Ti-based carbide), it was found that the work load during bending can be reduced while the wear resistance is secured, that is, the bending workability can be improved.

본 발명은 얻어진 지견을 기초로 더욱 검토를 더하여 이루어진 것으로, 즉, 본 발명은,The present invention has been made on the basis of further obtained knowledge, that is, the present invention,

1. 질량％ 로, C : 0.05 ～ 0.35 ％, Si : 0.05 ～ 1.0 ％, Mn : 0.1 ～ 2.0 ％, Ti : 0.1 ～ 1.2 ％, Al : 0.1 ％ 이하, 추가로 Cu : 0.1 ～ 1.0 ％, Ni : 0.1 ～ 2.0 ％, Cr : 0.1 ～ 1.0 ％, Mo : 0.05 ～ 1.0 ％, W : 0.05 ～ 1.0 ％, B : 0.0003 ～ 0.0030 ％ 의 1 종 또는 2 종 이상을 함유하고, (1) 식으로 나타내는 DI* 가 60 미만이고, 잔부 Fe 및 불가피적 불순물로 이루어지는 가공성이 우수한 내마모 강판.1. By mass%, C: 0.05 to 0.35%, Si: 0.05 to 1.0%, Mn: 0.1 to 2.0%, Ti: 0.1 to 1.2%, Al: 0.1% or less, further Cu: 0.1 to 1.0%, Ni 0.1 to 2.0%, Cr: 0.1 to 1.0%, Mo: 0.05 to 1.0%, W: 0.05 to 1.0%, B: 0.0003 to 0.0030%, containing one or two or more, represented by the formula (1) A wear-resistant steel sheet having a DI * of less than 60 and excellent workability including residual Fe and unavoidable impurities.

DI* ＝ 33.85 × (0.1 × C*)0.5 × (0.7 × Si ＋ 1) × (3.33 × Mn ＋ 1) × (0.35 × Cu ＋ 1) × (0.36 × Ni ＋ 1) × (2.16 × Cr ＋ 1) × (3 × Mo* ＋ 1) × (1.5 × W* ＋ 1) …… (1)DI * = 33.85 × (0.1 × C *) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo * + 1) × (1.5 × W * + 1). ... (One)

단, C* ＝ C － 1/4 × (Ti － 48/14N), Mo* ＝ Mo × (1 － 0.5 × (Ti － 48/14N)), W* ＝ W × (1 － 0.5 × (Ti － 48/14N))However, C * = C-1/4 × (Ti-48 / 14N), Mo * = Mo × (1-0.5 × (Ti-48 / 14N)), W * = W × (1-0.5 × (Ti (48 / 14N))

C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N 은 함유량 (mass％)C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N silver content (mass%)

2. 추가로, mass％ 로 Nb : 0.005 ～ 1.0 ％, V : 0.005 ～ 1.0 ％ 의 1 종 또는 2 종을 함유하는 것을 특징으로 하는 1 에 기재된 내마모 강판.2. Furthermore, the wear resistant steel plate of 1 characterized by containing 1 type or 2 types of Nb: 0.005-1.0%, V: 0.005-1.0% by mass%.

3. 추가로, 금속 조직이 페라이트-펄라이트상을 기지상으로 하고, 그 기지상 중에 경질상이 분산되어 있는 것을 특징으로 하는 1 또는 2 에 기재된 내마모 강판.3. The wear resistant steel sheet according to 1 or 2, wherein the metal structure has a ferrite-pearlite phase as a base phase and a hard phase is dispersed in the base phase.

4. 추가로, 상기 경질상의 분산 밀도가 400 개/㎟ 이상인 것을 특징으로 하는 3 에 기재된 내마모 강판.4. The wear-resistant steel sheet according to 3, wherein the hard phase has a dispersion density of 400 particles / mm 2 or more.

5. 1 또는 2 에 기재된 조성을 갖는 강편을 열간 압연 후, 2 ℃/s 이하의 냉각 속도로 400 ℃ 이하까지 냉각시키는 것을 특징으로 하는 가공성이 우수한 내마모 강판의 제조 방법.5. After hot-rolling a steel piece which has a composition as described in 1 or 2, it cools to 400 degrees C or less at the cooling rate of 2 degrees C / s or less, The manufacturing method of the wear resistant steel plate excellent in workability.

6. 추가로, 열간 압연에서의, 920 ℃ 이하에서의 압하율을 30 ％ 이상으로 하고, 압연 종료 온도를 900 ℃ 이하로 하는 것을 특징으로 하는 5 에 기재된 가공성이 우수한 내마모 강의 제조 방법.6. Furthermore, the rolling reduction temperature in 920 degreeC or less in hot rolling is made into 30% or more, and rolling end temperature is 900 degrees C or less, The manufacturing method of the wear resistant steel excellent in the workability of 5 characterized by the above-mentioned.

또한, 여기서, 상기 경질상은 TiC 등의 Ti 계 탄화물로 하는 것이 바람직하고, TiC, (NbTi)C, (VTi)C, 또는 TiC 중에 Mo, W 가 고용된 것을 예시할 수 있다.In this case, the hard phase is preferably made of Ti-based carbide such as TiC, and it is exemplified that Mo, W is dissolved in TiC, (NbTi) C, (VTi) C, or TiC.

본 발명에 의하면, 내마모성을 열화시키지 않고 굽힘 가공성을 향상시킨 내마모 강판이 열간 압연 후 열처리를 실시하지 않고 얻어지므로, 열처리 비용 저감 및 제조 공기 단축 등의 합리적인 생산이 가능하여 산업상 각별한 효과를 발휘한다.According to the present invention, since the wear-resistant steel sheet having improved bending workability without deterioration of wear resistance is obtained without performing heat treatment after hot rolling, it is possible to produce rational production such as reducing the heat treatment cost and shortening the manufacturing air, thereby exerting a special effect in the industry. do.

도 1 은 내마모성에 미치는 Ti 첨가량의 영향을 나타내는 도면이다.BRIEF DESCRIPTION OF THE DRAWINGS It is a figure which shows the effect of Ti addition amount on abrasion resistance.

도 2 는 인장 특성 (항복 강도 (yield strength) : YS, 인장 강도 (tensile strength) : TS) 에 미치는 Ti 첨가량의 영향을 나타내는 도면이다.2 is a diagram showing the effect of the amount of Ti added on the tensile properties (yield strength: YS, tensile strength: TS).

도 3 은 내마모성에 미치는 DI* 의 영향을 나타내는 도면이다.3 is a diagram showing the influence of DI * on wear resistance.

도 4 는 인장 특성 (항복 강도 : YS, 인장 강도 : TS) 에 미치는 DI* 의 영향을 나타내는 도면이다.4 is a diagram showing the influence of DI * on tensile properties (yield strength: YS, tensile strength: TS).

발명을 실시하기 위한 최선의 형태Best Mode for Carrying Out the Invention

본 발명에 관련된 내마모 강판에서 성분 조성, 금속 조직을 규정한 이유에 대해 설명한다.The reason why the component composition and the metal structure are defined in the wear resistant steel sheet according to the present invention will be described.

(성분 조성) 이하의 ％ 표시는, 모두 mass％ 로 한다.(Component composition) All the following% displays shall be mass%.

C : 0.05 ～ 0.35 ％C: 0.05 to 0.35%

C 는, 금속 조직에 있어서 매트릭스의 경도를 향상시켜 내마모성을 향상시킴과 함께, 경질인 제 2 상 (이하, 경질상이라고도 한다) 으로서의 Ti 탄화물을 형성하여, 내마모성의 향상에 유효한 원소로, 이와 같은 효과를 얻기 위해서는 0.05 ％ 이상의 함유를 필요로 한다.C is an element effective in improving the wear resistance by forming Ti carbide as a hard second phase (hereinafter also referred to as a hard phase) while improving the hardness of the matrix in the metal structure to improve wear resistance. In order to acquire an effect, 0.05% or more of containing is required.

한편, 0.35 ％ 를 초과하는 C 의 함유는, 경질상으로서의 탄화물이 조대해 져, 굽힘 가공시에 탄화물을 기점으로 하여 균열이 발생한다. 이 때문에, C 는 0.05 ～ 0.35 ％ 의 범위로 규정하였다. 또한, 바람직하게는 0.15 ～ 0.32 ％ 이다.On the other hand, in C containing more than 0.35%, carbide as a hard phase becomes coarse, and a crack arises from a carbide as a starting point at the time of bending process. For this reason, C was prescribed | regulated in 0.05 to 0.35% of range. Moreover, Preferably it is 0.15 to 0.32%.

Ti : 0.1 ～ 1.2 ％Ti: 0.1 to 1.2%

Ti 는, C 와 함께 본 발명에 있어서의 중요한 원소로, 내마모성 향상에 기여하는 경질상으로서 Ti 탄화물을 형성하는 필수 원소이다. 이와 같은 효과를 얻기 위해서는 0.1 ％ 이상의 함유를 필요로 한다.Ti, together with C, is an important element in the present invention and is an essential element for forming Ti carbide as a hard phase that contributes to improvement of wear resistance. In order to acquire such an effect, 0.1% or more of containing is required.

도 1 에 내마모성에 미치는 Ti 첨가량의 영향을, 도 2 에 인장 특성 (항복 강도 : YS, 인장 강도 : TS) 에 미치는 Ti 첨가량의 영향을 나타낸다. 도 1 에 있어서 종축은 러버 휠 마모 시험 (rubber wheel abrasion test) 에 있어서의 마모량을 연강 (mild steel) (SS400) 의 마모 감량 (abrasion weight loss) 과 비교한 내마모비를 나타낸다.The influence of the Ti addition amount on wear resistance in FIG. 1 is shown, and the influence of the Ti addition amount on tensile properties (yield strength: YS, tensile strength: TS) is shown in FIG. In Fig. 1, the vertical axis represents the wear resistance in comparison with the abrasion weight loss of the mild steel (SS400) in the rubber wheel abrasion test.

Ti 첨가량이 0.1 ％ 이상에서, 내마모성이 일반적인 내마모 강과 동일한 정도 이상의 특성이 얻어지고, 또한 TS 가 800 ㎫ 이하까지 저하되었다. 즉, 종래의 담금질 열처리를 한 내마모 강판과 동등한 마모 특성을 가지면서, 가공성을 개선할 수 있게 된다.At 0.1% or more of Ti addition amount, the characteristics of the wear resistance or more similar to the general wear-resistant steel were acquired, and TS fell to 800 Mpa or less. That is, while having wear characteristics equivalent to those of a wear-resistant steel sheet subjected to conventional quenching heat treatment, it is possible to improve workability.

러버 휠 마모 시험에 있어서의 공시 강은, mass％ 로 0.33 ％ C - 0.35 ％ Si - 0.82 ％ Mn - 0.05 ～ 1.2 ％ Ti 를 함유하는 강편을 19 mmt 로 압연 후, 냉각 속도 : 0.5 ℃/s 로 공랭시켜 제조하였다.The test steel in the rubber wheel abrasion test was obtained by rolling a steel piece containing 0.33% C-0.35% Si-0.82% Mn-0.05-1.2% Ti in mass% to 19 mmt, and then cooling rate: 0.5 ° C / s. Prepared by air cooling.

얻어진 강판에 대해 인장 시험 및 마모 시험을 실시하였다. 인장 시험 은, JIS Z 2201 의 규정에 준거하여 JIS 5 호 시험편을 채취하고 인장 시험을 실시하여, 인장 특성 (인장 강도 : TS, 항복 강도 : YS) 을 구하였다.The obtained steel sheet was subjected to a tensile test and a wear test. In the tensile test, a JIS No. 5 test piece was taken in accordance with the provisions of JIS Z 2201, a tensile test was performed, and tensile properties (tensile strength: TS, yield strength: YS) were obtained.

마모 시험은 ASTM G 65 에 준거한 러버 휠 마모 시험에 의해 실시하고, 시험 결과를 연강 (SS400) 의 마모량과 각 공시 강판의 마모량의 비를 내마모비로서 정리하였다. 내마모비가 클수록 마모 특성이 우수함을 나타낸다.The abrasion test was carried out by a rubber wheel abrasion test according to ASTM G 65, and the test results were summarized as abrasion resistance ratio of the amount of wear of mild steel (SS400) and the amount of wear of each steel sheet. The greater the wear resistance, the better the wear characteristics.

비교 시험으로서, 일반적인 열처리로 제조하는 내마모 강판에 대해서도 상기와 동일한 시험을 실시하였다. 얻어진 결과를 도 1 과 도 2 에 종래 강으로 나타낸다. 여기서 말하는 일반적인 내마모 강판이란, 0.15 mass％ C - 0.35 mass％ Si - 1.50 mass％ Mn - 0.13 mass％ Cr - 0.13 mass％ Mo - 0.01 mass％ Ti - 0.0010 mass％ B 조성의 강판을 열간 압연한 후, 900 ℃ 로 재가열 후, 담금질 열처리를 실시한 재료로, 브리넬 경도로 400 HB 정도의 강판을 가리킨다.As a comparative test, the same test as above was performed also about the wear-resistant steel plate manufactured by general heat processing. The obtained result is shown by the conventional steel in FIG. 1 and FIG. The general wear-resistant steel sheet herein refers to 0.15 mass% C-0.35 mass% Si-1.50 mass% Mn-0.13 mass% Cr-0.13 mass% Mo-0.01 mass% Ti-0.0010 mass% B after hot rolling , The material subjected to the quenching heat treatment after reheating to 900 ℃, refers to a steel plate of about 400 HB in Brinell hardness.

한편, Ti 의 함유량이 1.2 ％ 를 초과하는 함유는, 경질상 (Ti 계 탄화물) 이 조대화되어, 굽힘 가공시에 조대한 경질상을 기점으로 하여 균열이 발생한다. 이 때문에, Ti 는 0.1 ～ 1.2 ％, 바람직하게는 0.1 ～ 0.8 ％ 의 범위로 한정하였다. On the other hand, in the case where the Ti content is more than 1.2%, the hard phase (Ti-based carbide) is coarsened, and cracking occurs starting from the coarse hard phase at the time of bending. For this reason, Ti was 0.1 to 1.2%, Preferably it was limited to the range of 0.1 to 0.8%.

Si : 0.05 ～ 1.0 ％Si: 0.05 to 1.0%

Si 는 탈산 원소 (deoxidizing element) 로서 유효한 원소로, 이와 같은 효과를 얻기 위해서는 0.05 ％ 이상의 함유를 필요로 한다. 또한, Si 는 강에 고용되어 고용 강화에 의해 고경도화에 기여하는 유효한 원소인데, 1.0 ％ 를 초과하는 함유는 연성 (ductility), 인성 (toughness) 을 저하시키고, 더욱 개재물량 (inclusion content) 이 증가하는 등의 문제를 발생시킨다. 이 때문에, Si 는 0.05 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.05 ～ 0.40 ％ 이다.Si is an effective element as a deoxidizing element, and in order to obtain such an effect, it needs to contain 0.05% or more. In addition, Si is an effective element that is dissolved in steel and contributes to high hardness by solid solution strengthening. A content exceeding 1.0% decreases ductility and toughness, and further increases inclusion content. To cause problems. For this reason, it is preferable to limit Si to 0.05 to 1.0% of range. Moreover, More preferably, it is 0.05 to 0.40%.

Mn : 0.1 ～ 2.0 ％Mn: 0.1 to 2.0%

Mn 은 고용 강화에 의해 고경도화에 기여하는 유효한 원소로, 이와 같은 효과를 얻기 위해서는 0.1 ％ 이상의 함유를 필요로 한다. 한편, 2.0 ％ 를 초과하는 함유는 용접성을 저하시킨다. 이 때문에, Mn 은 0.1 ～ 2.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 1.60 ％ 이다.Mn is an effective element contributing to high hardness by solid solution strengthening, and in order to obtain such an effect, 0.1% or more of Mn is required. On the other hand, containing exceeding 2.0% reduces weldability. For this reason, it is preferable to limit Mn to 0.1 to 2.0% of range. Moreover, More preferably, it is 0.1 to 1.60%.

Al : 0.1 ％ 이하Al: 0.1% or less

Al 은 탈산 원소 (deoxidizing element) 로서 작용하고, 이와 같은 효과는 0.0020 ％ 이상의 함유에서 관찰되는데, 0.1 ％ 를 초과하는 다량의 함유는 강의 청정도 (cleanness) 를 저하시킨다. 이 때문에, Al 은 0.1 ％ 이하로 한정하는 것이 바람직하다.Al acts as a deoxidizing element, and this effect is observed at a content of 0.0020% or more, with a large amount of content exceeding 0.1% lowering the cleanness of the steel. For this reason, it is preferable to limit Al to 0.1% or less.

Cu : 0.1 ～ 1.0 ％, Ni : 0.1 ～ 2.0 ％, Cr : 0.1 ～ 1.0 ％, Mo : 0.05 ～ 1.0 ％, W : 0.05 ～ 1.0 ％, B : 0.0003 ～ 0.0030 ％ 의 1 종 또는 2 종 이상Cu: 0.1% to 1.0%, Ni: 0.1% to 2.0%, Cr: 0.1% to 1.0%, Mo: 0.05% to 1.0%, W: 0.05% to 1.0%, B: 0.0003% to 0.0030%.

Cu : 0.1 ～ 1.0 ％Cu: 0.1% to 1.0%

Cu 는 고용됨으로써 담금질성 (hardenability) 을 향상시키는 원소로, 이 효과를 얻기 위해서는 0.1 ％ 이상의 함유를 필요로 한다. 한편, 1.0 ％ 를 초과하는 함유는 열간 가공성을 저하시킨다. 이 때문에, Cu 는 0.1 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 0.5 ％ 이 다.Cu is an element which improves hardenability by solid solution and requires 0.1% or more to obtain this effect. On the other hand, containing exceeding 1.0% reduces hot workability. For this reason, it is preferable to limit Cu to 0.1 to 1.0% of range. Moreover, More preferably, it is 0.1 to 0.5%.

Ni : 0.1 ～ 2.0 ％Ni: 0.1 to 2.0%

Ni 는 고용됨으로써 담금질성을 향상시키는 원소로, 이와 같은 효과는 0.1 ％ 이상의 함유에서 현저해진다. 한편, 2.0 ％ 를 초과하는 함유는 재료 비용을 현저하게 상승시킨다. 이 때문에, Ni 는 0.1 ～ 2.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 1.0 ％ 이다.Ni is an element which improves hardenability by solid solution, and such an effect becomes remarkable when it contains 0.1% or more. On the other hand, containing exceeding 2.0% raises material cost remarkably. For this reason, it is preferable to limit Ni to 0.1 to 2.0% of range. Moreover, More preferably, it is 0.1 to 1.0%.

Cr : 0.1 ～ 1.0 ％Cr: 0.1% to 1.0%

Cr 은 담금질성을 향상시키는 효과를 갖고, 이와 같은 효과를 얻기 위해서는 0.1 ％ 이상의 함유를 필요로 하는데, 1.0 ％ 를 초과하는 함유는 용접성을 저하시킨다. 이 때문에, Cr 은 0.1 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 0.8 ％ 이다. 더욱 바람직하게는 0.4 ～ 0.7 ％ 이다.Cr has the effect of improving hardenability, and in order to acquire such an effect, 0.1% or more of content is required, but the content exceeding 1.0% reduces weldability. For this reason, it is preferable to limit Cr to 0.1 to 1.0% of range. Moreover, More preferably, it is 0.1 to 0.8%. More preferably, it is 0.4 to 0.7%.

Mo : 0.05 ～ 1.0 ％Mo: 0.05 to 1.0%

Mo 는 담금질성을 향상시키는 원소이다. 이와 같은 효과를 얻기 위해서는 0.05 ％ 이상의 함유를 필요로 한다. 한편, 1.0 ％ 를 초과하여 함유하면 용접성을 저하시킨다. 그 때문에, Mo 는 0.05 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.05 ～ 0.40 ％ 이다.Mo is an element which improves hardenability. In order to acquire such an effect, 0.05% or more of containing is required. On the other hand, when it contains exceeding 1.0%, weldability will fall. Therefore, it is preferable to limit Mo to 0.05 to 1.0% of range. Moreover, More preferably, it is 0.05 to 0.40%.

W : 0.05 ～ 1.0 ％W: 0.05 to 1.0%

W 는 담금질성을 향상시키는 원소이다. 이와 같은 효과를 얻기 위해서는 0.05 ％ 이상의 함유를 필요로 한다. 한편, 1.0 ％ 를 초과하여 함유하면 용접 성을 저하시킨다. 그 때문에, W 는 0.05 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.05 ～ 0.40 ％ 이다. 또한, Mo 나 W 는 TiC 에 고용되기 때문에, 경질상의 양을 증가시키는 효과도 갖는다.W is an element which improves hardenability. In order to acquire such an effect, 0.05% or more of containing is required. On the other hand, when it contains exceeding 1.0%, weldability will fall. Therefore, it is preferable to limit W to 0.05 to 1.0% of range. Moreover, More preferably, it is 0.05 to 0.40%. In addition, since Mo and W are dissolved in TiC, the amount of the hard phase is also increased.

B : 0.0003 ～ 0.0030 ％B: 0.0003 to 0.0030%

B 는 입계 (grain boundary) 에 편석되고, 입계를 강화시켜 인성 향상에 유효하게 기여하는 원소로, 이와 같은 효과를 얻기 위해서는 0.0003 ％ 이상의 함유가 필요하다. 한편, 0.0030 ％ 를 초과하는 함유는 용접성을 저하시킨다. 이 때문에, B 는 0.0003 ～ 0.0030 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.0003 ～ 0.0015 ％ 이다.B is an element that segregates at grain boundaries and effectively contributes to toughness improvement by strengthening grain boundaries. In order to obtain such an effect, the B content needs to be 0.0003% or more. On the other hand, containing exceeding 0.0030% reduces weldability. For this reason, it is preferable to limit B to 0.0003 to 0.0030% of range. More preferably, it is 0.0003 to 0.0015%.

DI* ＜ 60DI * <60

본 발명에서 DI* (담금질성 지표값 (hardenability index)) 는, DI* ＝ 33.85 × (0.1 × C*)0.5 × (0.7 × Si ＋ 1) × (3.33 × Mn ＋ 1) × (0.35 × Cu ＋ 1) × (0.36 × Ni ＋ 1) × (2.16 × Cr ＋ 1) × (3 × Mo* ＋ 1) × (1.5 × W* ＋ 1), 여기서 C* ＝ C － 1/4 × (Ti － 48/14N), Mo* ＝ Mo × (1 － 0.5 × (Ti － 48/14N)), W* ＝ W × (1 － 0.5 × (Ti － 48/14N)) 으로 정의하고, DI* ＜ 60 으로 한다. 여기서, C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N 은 함유량 (mass％) 이다. 도 3 에 내마모성에 미치는 DI* 의 영향을, 도 4 에 인장 특성 (항복 강도 : YS, 인장 강도 : TS) 에 미치는 DI* 의 영향을 나타낸다. 도 3 에 있어서 종축은 러버 휠 마모 시험에 있어서의 마모량을 연강 (SS400) 의 마모량과 비교한 내마모비를 나타낸다. 내마모비가 클수록 마모 특성이 우수함을 나타낸다.In the present invention, DI * (hardenability index) is DI * = 33.85 × (0.1 × C *) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo * + 1) × (1.5 × W * + 1), where C * = C-1/4 × (Ti -48 / 14N), Mo * = Mo x (1-0.5 x (Ti-48 / 14N)), W * = W x (1-0.5 x (Ti-48 / 14N)), and DI * < To 60. Here, C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, and N are content (mass%). The influence of DI * on wear resistance in FIG. 3 is shown, and the influence of DI * on tensile properties (yield strength: YS, tensile strength: TS) is shown in FIG. In FIG. 3, the vertical axis | shaft shows an abrasion-resistance ratio which compared the wear amount in the rubber wheel abrasion test with the wear amount of mild steel (SS400). The greater the wear resistance, the better the wear characteristics.

도 3 및 도 4 로부터, DI* 가 60 미만인 경우, 인장 강도 : TS 가 800 ㎫ 이하로 저강도임에도 불구하고, 마모량이 일반적인 내마모 강과 동일한 정도인 것이 확인된다.3 and 4, when DI * is less than 60, although the tensile strength: TS is 800 MPa or less and low strength, it is confirmed that the amount of wear is about the same as that of general wear-resistant steel.

한편, DI* 가 60 이상에서는, 마모성은 우수하지만, 인장 강도가 800 ㎫ 이상으로 가공성이 떨어진다. DI* 가 60 이상인 경우, 페라이트-베이나이트 조직 (ferrite and bainite structure) 이 되기 때문인 것으로 추측된다.On the other hand, when DI * is 60 or more, although abrasion property is excellent, workability is inferior to 800 Mpa or more of tensile strength. If DI * is 60 or more, it is presumed to be a ferrite and bainite structure.

러버 휠 마모 시험에 있어서의 공시 강은, mass％ 로 0.34 ％ C - 0.22 ％ Si - 0.55 ％ Mn - 0.22 ％ Ti 에 추가로 Cu, Ni, Cr, Mo, W 의 1 종 또는 2 종 이상 함유하고, DI* 가 40 ～ 120 인 강편을 8 mmt 로 압연 후, 공랭 (냉각 속도 : 1.2 ℃/s) 시켜 제조하였다.The test steel in the rubber wheel abrasion test contains 0.34% C-0.22% Si-0.55% Mn-0.22% Ti, in addition to Cu, Ni, Cr, Mo, W, or one or two or more, in mass%. And DI * of 40-120 were rolled to 8 mmt, and air cooled (cooling rate: 1.2 degree-C / s) and manufactured.

얻어진 강판에 대해 인장 시험 및 마모 시험을 실시하였다. 인장 시험은, JlS Z 2201 의 규정에 준거하여 JIS 5 호 시험편을 채취하고 인장 시험을 실시하여, 인장 특성 (인장 강도 TS, 항복 강도 YS) 을 구하였다.The obtained steel sheet was subjected to a tensile test and a wear test. In the tensile test, the JIS No. 5 test piece was taken in accordance with the provisions of JlS Z 2201, a tensile test was performed, and tensile properties (tensile strength TS, yield strength YS) were obtained.

러버 휠 마모 시험은 ASTM G 65 에 준거하여 실시하고, 시험 결과는 연강 (SS400) 의 마모량과 각 강판의 마모량의 비를 내마모비로서 정리하였다.The rubber wheel abrasion test was carried out in accordance with ASTM G 65, and the test results were summarized as abrasion resistance ratio of the wear amount of mild steel (SS400) and the wear amount of each steel plate.

상기한 성분이 기본 성분으로 우수한 내마모성이 얻어지는데, 본 발명에서는 더욱 내마모성을 향상시키기 위해, 경질인 제 2 상을 형성하고, 내마모성에 기여하는 원소인 Nb, V 를 선택 원소로서 함유할 수 있다.Although the above-described component obtains excellent wear resistance as a basic component, in the present invention, in order to further improve wear resistance, the hard second phase may be formed, and Nb and V, which are elements contributing to wear resistance, may be included as a selection element.

Nb : 0.005 ～ 1.0 ％,Nb: 0.005 to 1.0%,

Nb 는, Ti 와 복합하여 첨가함으로써 Ti, Nb 의 복합 탄화물 ((NbTi)C) 을 형성하고, 경질인 제 2 상으로서 분산되어, 내마모성 향상에 유효하게 기여하는 원소이다. 이와 같은 내마모성 향상 효과를 얻기 위해서는 0.005 ％ 이상의 함유를 필요로 한다. 한편, 1.0 ％ 를 초과하는 함유는, 경질인 제 2 상 (Ti, Nb 의 복합 탄화물) 이 조대화되어, 굽힘 가공시에 경질인 제 2 상 (Ti, Nb 의 복합 탄화물) 을 기점으로 하여 균열이 발생한다. 이 때문에, 첨가하는 경우에는 Nb 는 0.005 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 0.5 ％ 이다.Nb is an element which forms a composite carbide ((NbTi) C) of Ti and Nb by complex addition with Ti, is dispersed as a hard second phase, and effectively contributes to the improvement of wear resistance. In order to acquire such abrasion resistance improvement effect, 0.005% or more of containing is required. On the other hand, the content exceeding 1.0% is that the hard second phase (composite carbides of Ti and Nb) is coarsened and cracks based on the hard second phase (combined carbides of Ti and Nb) during bending. This happens. For this reason, when adding, it is preferable to limit Nb to 0.005 to 1.0% of range. Moreover, More preferably, it is 0.1 to 0.5%.

V : 0.005 ～ 1.0 ％V: 0.005 to 1.0%

V 는, Ti 와 복합하여 첨가함으로써 Nb 와 동일하게 Ti, V 의 복합 탄화물 ((VTi)C) 을 형성하고, 경질인 제 2 상으로서 분산되어, 내마모성 향상에 유효하게 기여하는 원소이다. 이와 같은 내마모성 향상 효과를 얻기 위해서는 0.005 ％ 이상의 함유를 필요로 한다. V is an element that forms a composite carbide ((VTi) C) of Ti and V in the same manner as Nb by adding it in combination with Ti, is dispersed as a hard second phase, and effectively contributes to the improvement of wear resistance. In order to acquire such abrasion resistance improvement effect, 0.005% or more of containing is required.

한편, 1.0 ％ 를 초과하는 함유는, 경질인 제 2 상 (Ti, V 의 복합 탄화물) 이 조대화되어, 굽힘 가공시에 경질인 제 2 상 (Ti, V 의 복합 탄화물) 을 기점으로 하여 균열이 발생한다. 이 때문에, 첨가하는 경우에는 V 는 0.005 ～ 1.0 ％ 의 범위로 한정하는 것이 바람직하다. 또한, 보다 바람직하게는 0.1 ～ 0.5 ％ 이다.On the other hand, the content exceeding 1.0% is that the hard second phase (composite carbides of Ti and V) is coarsened and cracks based on the hard second phase (combined carbides of Ti and V) during bending. This happens. For this reason, when adding, it is preferable to limit V to 0.005 to 1.0% of range. Moreover, More preferably, it is 0.1 to 0.5%.

또한, Nb 와 V 를 복합하여 첨가하는 경우에는, 경질인 제 2 상이 (NbVTi)C 가 되는 것만으로, 동일하게 내마모성을 향상시키는 효과를 갖는다. 또한, N 을 함유하는 경우에는, 탄화물 외에 탄질화물이 형성되는 경우도 있지만, 동일한 효과가 얻어진다.In addition, when Nb and V are added in combination, only the hard second phase becomes (NbVTi) C, and thus has an effect of improving abrasion resistance. In addition, when N contains, in addition to carbide, carbonitride may be formed, but the same effect is acquired.

단, N 첨가량이 0.01 ％ 를 초과하는 경우에는, 탄질화물 중의 N 비율이 증가하여 경질 제 2 상의 경도가 저하되는데, 내마모성의 열화가 우려된다. 따라서, N 첨가량은 0.01 ％ 이하로 하는 것이 바람직하다.However, when N addition amount exceeds 0.01%, although the N ratio in carbonitride increases and the hardness of a hard 2nd phase falls, there exists a possibility of deterioration of abrasion resistance. Therefore, it is preferable to make N addition amount into 0.01% or less.

(금속 조직)(Metal structure)

본 발명에 관련된 내마모 강판은, 금속 조직을, 페라이트-펄라이트상을 기지상으로 하고, 당해 기지상 중에 경질상 (경질인 제 2 상) 이 분산된 조직으로 한다. 기지상이란 체적률로 90 ％ 이상 갖는 것을 의미하며, 본 발명에 관련된 강판은 페라이트와 펄라이트의 2 개의 상이 전체의 90 ％ 이상을 차지하고 있다.The wear resistant steel sheet which concerns on this invention makes a metal structure into a structure where a ferrite-perlite phase is known phase and the hard phase (hard second phase) was disperse | distributed in the said base phase. The matrix phase means having 90% or more by volume ratio, and in the steel sheet according to the present invention, two phases of ferrite and pearlite occupy 90% or more of the whole.

또한, 그 중 페라이트상의 체적률은 70 ％ 이상이고, 또한 원 상당 직경으로 평균 입경 20 ㎛ 의 페라이트상인 것이 바람직하다. 기지상은 가공성을 고려하여, 브리넬 경도로 300 HB 이하로 하는 것이 바람직하다.In addition, the volume ratio of a ferrite phase is 70% or more, and it is preferable that it is a ferrite phase with an average particle diameter of 20 micrometers in circular equivalent diameter. It is preferable to make a known phase into 300 HB or less by Brinell hardness in consideration of workability.

경질상으로는, TiC 등의 Ti 계 탄화물로 하는 것이 바람직하고, TiC, (NbTi)C, (VTi)C, 또는 TiC 중에 Mo, W 가 고용된 것을 예시할 수 있다.As a hard phase, it is preferable to set it as Ti type carbides, such as TiC, and the thing which Mo, W was solid-solution in TiC, (NbTi) C, (VTi) C, or TiC can be illustrated.

또한, 경질상의 크기는 특별히 한정되지 않지만, 내마모성의 관점에서는 0.5 ㎛ 이상 50 ㎛ 이하 정도로 하는 것이 바람직하다. 또한, 경질상의 분산 밀도는 내마모성의 관점에서 400 개/㎟ 이상으로 하는 것이 바람직하다. The size of the hard phase is not particularly limited, but is preferably about 0.5 µm or more and 50 µm or less from the viewpoint of wear resistance. In addition, it is preferable that the dispersion density of a hard phase shall be 400 pieces / mm <2> or more from a viewpoint of abrasion resistance.

또한, 경질상의 크기는 각 경질상의 면적을 측정하고, 동일 면적으로부터 원 상당 직경을 산출하고, 얻어진 원 상당 직경을 산술 평균내어 평균값을 그 강판에 있어서의 경질상의 크기 (평균 입경) 로 한다.In addition, the size of a hard phase measures the area of each hard phase, calculates a circle equivalent diameter from the same area, arithmetic averages the obtained circle equivalent diameter, and makes an average value the size (average particle diameter) of the hard phase in the steel plate.

(제조 방법)(Manufacturing method)

본 발명에 관련된 내마모 강판은, 상기한 조성의 용강 (溶鋼) 을 공지된 용제 (溶製) 방법으로 용제하고, 연속 주조법 또는 조괴-분해 압연법에 의해 소정 치수의 슬래브 (slab) 등의 강 소재로 하는 것이 바람직하다.The wear resistant steel sheet which concerns on this invention melt | dissolves molten steel of the said composition by a well-known solvent method, and steels, such as slab of predetermined dimension, by the continuous casting method or the ingot-decomposition rolling method. It is preferable to set it as a raw material.

경질상을 소정의 크기 및 개수로 조정하기 위해서는, 예를 들어 연속 주조법을 사용한 경우, 두께 200 ～ 400 ㎜ 인 주편 (鑄片) 의 1500 ～ 1200 ℃ 온도역에 있어서의 냉각 속도 0.2 ～ 10 ℃/s 의 범위가 되도록 냉각을 조정하는 것이 바람직하다.In order to adjust a hard phase to a predetermined | prescribed size and number, when the continuous casting method is used, for example, the cooling rate in the 1500-1200 degreeC temperature range of the slab of 200-400 mm thickness is 0.2-10 degreeC / It is preferable to adjust cooling so that it may become the range of s.

또한, 조괴법을 사용하는 경우에도, 잉곳 (ingot) 의 크기 및 냉각 조건을, 경질상이 원하는 크기 및 개수가 되도록 조정할 필요가 있는 것은 말할 필요도 없다.In addition, even when using the ingot method, it goes without saying that it is necessary to adjust the size and cooling conditions of an ingot so that a hard phase may become desired size and number.

이어서, 강 소재를 냉각시키지 않고 바로 열간 압연하고, 또는 냉각 후 950 ～ 1250 ℃ 로 재가열한 후, 열간 압연하여 원하는 판두께의 강판으로 한다. 열간 압연 후에는, 열처리하지 않고 평균 냉각 속도 2 ℃/s 이하로 냉각시킨다.Next, hot rolling is performed immediately without cooling the steel material, or after reheating to 950 to 1250 ° C after cooling, hot rolling to obtain a steel sheet having a desired plate thickness. After hot rolling, it cools at 2 degrees C / s or less of average cooling rates, without heat processing.

냉각 속도가 2 ℃/s 를 초과하면, 페라이트-펄라이트 조직이 얻어지지 않고, 인장 강도가 800 ㎫ 이상이 되고, 강판 굽힘 가공시의 가공 하중이 상승하여, 가공성이 열화된다. 따라서, 2 ℃/s 이하로 한다.When the cooling rate exceeds 2 ° C / s, no ferrite-pearlite structure is obtained, the tensile strength is 800 MPa or more, the processing load during steel sheet bending processing increases, and workability is deteriorated. Therefore, you may be 2 degrees C / s or less.

또한, 열간 압연 조건은 원하는 치수 형상의 강판으로 할 수 있으면 되고, 특별히 한정되지 않지만, 강판으로서 구비해야 할 성능인 인성을 고려하면, 강판의 표면 온도에서, 920 ℃ 이하에서의 압하율을 30 ％ 이상으로 하고, 또한 압연 종료 온도를 900 ℃ 이하로 하는 것이 필요하다.In addition, hot rolling conditions should just be a steel plate of a desired dimension shape, Although it does not specifically limit, Considering the toughness which is the performance which should be provided as a steel plate, the rolling reduction in 920 degrees C or less is 30% at the surface temperature of a steel plate. It is necessary to make it into the above and to make rolling end temperature 900 degrees C or less.

본 발명에 관련된 내마모 강판은, 열간 압연 후에 열처리를 실시할 필요가 없어, 열간 압연의 상태에서 굽힘 가공을 필요로 하는 다양한 용도에 사용할 수 있다.The wear resistant steel sheet which concerns on this invention does not need to heat-process after hot rolling, and can be used for the various uses which require bending process in the state of hot rolling.

실시예Example

표 1 에 나타내는 조성의 용강을 진공 용해로에서 용제하여, 소형 강괴 (50 ㎏) (강 소재) 로 한 후, 1050 ～ 1250 ℃ 로 가열하고, 열간 압연을 실시하여 판두께 6 ～ 100 ㎜ 의 공시 강판으로 하였다. 각 공시 강판에 대해 조직 관찰, 인장 시험 (tensile test), 마모 시험, 샤르피 충격 시험 (Charpy impact test), 굽힘 시험 (bend test) 을 실시하였다.The molten steel of the composition shown in Table 1 was melted in a vacuum melting furnace, it was made into a small ingot (50 kg) (steel material), and it heated at 1050-1250 degreeC, hot-rolled, and the steel plate of the thickness of 6-100 mm It was made. The steel sheet was subjected to structure observation, tensile test, abrasion test, Charpy impact test, and bend test.

(조직 관찰)(Tissue observation)

조직 관찰용 시험편은, 연마 후 나이탈 (nital) 부식시키고, 표층하 1 ㎜ 의 위치에 대해, 광학 현미경 (optical microscope) (배율 (magnification ratio) : 400 배) 을 사용하여 조직의 동정 (同定), 페라이트 입경 (ferrite grain diameter) 및 경질상의 크기, 개수를 측정하였다. 또한, 관찰 시야에 있어서 90 ％ 이상을 차지하는 조직을 기지상으로 하고, 경질상의 크기는 전술한 방법에 의해 구한 평균 입경으로 하였다.The specimen for tissue observation was subjected to nitrial corrosion after polishing and identification of the tissue using an optical microscope (magnification ratio: 400 times) at a position of 1 mm under the surface layer. , Ferrite grain diameter and size and number of hard phases were measured. In addition, the structure which occupies 90% or more in an observation visual field was made into the base phase, and the size of the hard phase was made into the average particle diameter calculated | required by the method mentioned above.

(인장 시험)(Tension test)

JIS Z 2201 의 규정에 준거하여 JIS 5 호 시험편을 채취하고, JIS Z 2241 의 규정에 준거하여 인장 시험을 실시하여, 인장 특성 (항복 강도 : YS, 인장 강도 : TS) 을 구하였다. 인장 강도 (TS) ＜ 800 ㎫, 항복 강도 (YS) ＜ 600 ㎫ 를 본 발명 범위로 한다.A JIS No. 5 test piece was sampled in accordance with JIS Z 2201, a tensile test was performed in accordance with JIS Z 2241, and tensile properties (yield strength: YS, tensile strength: TS) were obtained. Tensile strength (TS) <800 MPa and yield strength (YS) <600 MPa are made into this invention range.

(마모 시험)(Wear test)

시험편은 t (판두께) × 20 × 75 (㎜) 로 하고, ASTM G 65 의 규정에 준거하여 러버 휠 마모 시험을, 마모 모래 (abrasive sand) 를 사용하여 실시하였다. 시험 후, 시험편의 마모량을 측정하였다.The test piece was t (plate thickness) x 20 x 75 (mm), and the rubber wheel abrasion test was implemented using the abrasive sand based on ASTM G65. After the test, the amount of abrasion of the test piece was measured.

시험 결과는, 연강 (SS400) 판의 마모량을 기준 (1.0) 으로 하여, 내마모비 ＝ (연강판의 마모량) / (각 강판의 마모량) 으로 평가하였다. 내마모비가 클수록 내마모성이 우수함을 의미하며, 본 발명 범위는 내마모비 : 4.0 이상으로 하였다.The test result was evaluated based on the wear amount of the mild steel (SS400) plate as a reference (1.0), and abrasion ratio = (wear amount of the mild steel plate) / (wear amount of each steel plate). The greater the wear resistance, the better the wear resistance, and the scope of the present invention was set at abrasion resistance: 4.0 or more.

(샤르피 충격 시험)(Charpy impact test)

JIS Z 2202 의 규정에 준거하여, 판두께 방향 1/4 의 위치에서 L 방향으로 V 노치 충격 시험편을 채취하고, JIS Z 2242 의 규정에 준거하여, 시험 온도 0 ℃ 에서 샤르피 충격 시험을 실시하여 샤르피 흡수 에너지 (Charpy absorbed energy) 를 구하였다. 시험 개수는 3 개로 하고, 평균값을 구하였다.In accordance with the provisions of JIS Z 2202, the V-notch impact test piece was taken in the L direction at a position in the plate thickness direction 1/4, and subjected to the Charpy impact test at a test temperature of 0 ° C in accordance with the provisions of JIS Z 2242. The absorbed energy was calculated. The number of tests was made into three pieces and the average value was calculated | required.

(굽힘 시험)(Bending test)

JIS Z 2204 의 규정에 준거하여, 폭은 50 ㎜ 이고, 공시 강판의 판두께가 45 ㎜ 이상인 경우에는, 편면측에서 연삭하여 판두께 25 ㎜ 로 두께를 감소시킨 시험 편을 채취하고, 공시 강판의 판두께가 45 ㎜ 미만인 경우에는 판두께 그대로의 시험편을 채취하고, JIS Z 2248 의 규정에 준거하여 굽힘 시험을 실시하였다. 굽힘 시험은 프레싱 굽힘법으로 굽힘 반경을 r ＝ 1.5 t 로 하여 실시하였다.In accordance with the provisions of JIS Z 2204, when the width is 50 mm and the sheet thickness of the published steel sheet is 45 mm or more, a test piece ground on one side and reduced in thickness by 25 mm is taken, and the When the plate | board thickness was less than 45 mm, the test piece of the plate | board thickness as it is was taken, and the bending test was done based on the specification of JISZ2248. The bending test was carried out by pressing bending method with a bending radius of r = 1.5 t.

표 2 에 조직 관찰, 인장 시험, 마모 시험의 결과를 나타낸다. 본 발명예 (강판 No.1 ～ 6, 강판 No.8, 9) 는, 인장 강도 (TS) ＜ 800 ㎫, 항복 강도 (YS) ＜ 600 ㎫ 에도 불구하고, 내마모성이 매우 우수한 강판이 되었다.Table 2 shows the results of the structure observation, the tensile test, and the abrasion test. This invention example (steel plate No. 1-6, steel plate No. 8, 9) became a steel plate which was very excellent in abrasion resistance in spite of tensile strength (TS) <800 Mpa and yield strength (YS) <600 Mpa.

또한, 샤르피 흡수 에너지는, 압연 마무리 온도가 900 ℃ 이하인 경우에는 27 J 이상이었다. 한편, 비교예는 본 발명예와 비교하여 내마모성이 떨어지거나, 내마모성은 동등해도 YS, TS 가 높기 때문에 굽힘 가공성이 떨어진다.In addition, Charpy absorbed energy was 27 J or more when the rolling finish temperature was 900 degrees C or less. On the other hand, a comparative example is inferior in abrasion resistance compared with the example of this invention, or since bending resistance is inferior because YS and TS are high even if it is equivalent.

Figure 112009064203828-pct00001
Figure 112009064203828-pct00001

주 1 : * 표시 본 발명 범위 외Note 1: * outside the scope of the present invention

주 2 : DI* ＝ 33.85 × (0.1 × C*)0.5 × (0.7 × Si ＋ 1) × (3.33 × Mn ＋ 1) × (0.35 × Cu ＋ 1) × (0.36 × Ni ＋ 1) × (2.16 × Cr ＋ 1) × (3 × Mo* ＋ 1) × (1.5 × W* ＋ 1)Note 2: DI * = 33.85 × (0.1 × C *) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo * + 1) × (1.5 × W * + 1)

Figure 112009064203828-pct00002
Figure 112009064203828-pct00002

주 1 : * 표시 본 발명 범위 외Note 1: * outside the scope of the present invention

주 2 : 내마모비 (연강판의 마모량) / (각 강판의 마모량)Note 2: Abrasion resistance (wear amount of mild steel plate) / (wear amount of each steel plate)

(본 발명 범위 : 내마모비 4.0 이상)       (Scope of the present invention: wear resistance 4.0 or more)

Figure 112009064203828-pct00003
Figure 112009064203828-pct00003

주 1 : 내마모비 (연강판의 마모량) / (각 강판의 마모량)Note 1: Abrasion resistance (wear amount of mild steel plate) / (wear amount of each steel plate)

(본 발명 범위 : 내마모비 4.0 이상)       (Scope of the present invention: wear resistance 4.0 or more)

주 2 : vE0(J) : 시험 온도 0 ℃ 에서의 샤르피 충격 흡수 에너지 (J)Note 2: vE 0 (J): Charpy impact absorption energy at test temperature of 0 ° C (J)

Claims (6)

질량％ 로, C : 0.05 ～ 0.35 ％, Si : 0.05 ～ 1.0 ％, Mn : 0.1 ～ 2.0 ％, Ti : 0.1 ～ 1.2 ％, Al : 0.0020 ~ 0.1 ％, 추가로 Cu : 0.1 ～ 1.0 ％, Ni : 0.1 ～ 2.0 ％, Cr : 0.1 ～ 1.0 ％, Mo : 0.05 ～ 1.0 ％, W : 0.05 ～ 1.0 ％, B : 0.0003 ～ 0.0030 ％ 의 1 종 또는 2 종 이상을 함유하고, (1) 식으로 나타내는 DI* 가 60 미만이고, 잔부 Fe 및 불가피적 불순물로 이루어지고,In mass%, C: 0.05 to 0.35%, Si: 0.05 to 1.0%, Mn: 0.1 to 2.0%, Ti: 0.1 to 1.2%, Al: 0.0020 to 0.1%, Cu: 0.1 to 1.0%, Ni: DI containing 0.1 to 2.0%, Cr: 0.1 to 1.0%, Mo: 0.05 to 1.0%, W: 0.05 to 1.0%, B: 0.0003 to 0.0030%, or one or two or more, represented by the formula (1) * Is less than 60, consisting of residual Fe and inevitable impurities, 인장강도가 800 MPa 미만이며,Tensile strength is less than 800 MPa, 금속 조직이 체적율이 90 % 이상의 페라이트-펄라이트상을 기지상으로 하고, 그 기지상 중에 경질상이 분산되어 있는 내마모 강판.A wear resistant steel sheet in which a metal structure has a ferrite-pearlite phase having a volume ratio of 90% or more as a base phase, and a hard phase is dispersed in the base phase. DI* ＝ 33.85 × (0.1 × C*)0.5 × (0.7 × Si ＋ 1) × (3.33 × Mn ＋ 1) × (0.35 × Cu ＋ 1) × (0.36 × Ni ＋ 1) × (2.16 × Cr ＋ 1) × (3 × Mo* ＋ 1) × (1.5 × W* ＋ 1) …… (1)DI * = 33.85 × (0.1 × C *) 0.5 × (0.7 × Si + 1) × (3.33 × Mn + 1) × (0.35 × Cu + 1) × (0.36 × Ni + 1) × (2.16 × Cr + 1) × (3 × Mo * + 1) × (1.5 × W * + 1). ... (One) 단, C* ＝ C － 1/4 × (Ti － 48/14N), Mo* ＝ Mo × (1 － 0.5 × (Ti － 48/14N)), W* ＝ W × (1 － 0.5 × (Ti － 48/14N)), 여기서 C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N 은 함유량 (질량％)However, C * = C-1/4 × (Ti-48 / 14N), Mo * = Mo × (1-0.5 × (Ti-48 / 14N)), W * = W × (1-0.5 × (Ti -48 / 14N)), where C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, and N are content (mass%) 제 1 항에 있어서,The method of claim 1, 추가로, 질량％ 로 Nb : 0.005 ～ 1.0 ％, V : 0.005 ～ 1.0 ％ 의 1 종 또는 2 종을 함유하는 내마모 강판.Furthermore, the wear-resistant steel plate which contains 1 type or 2 types of Nb: 0.005-1.0%, V: 0.005-1.0% by mass%. 삭제delete 제 1 항 또는 제 2 항에 있어서,3. The method according to claim 1 or 2, 추가로, 상기 경질상의 분산 밀도가 400 개/㎟ 이상인 내마모 강판.Further, the hard steel sheet has a dispersion density of at least 400 particles / mm 2. 제 1 항 또는 제 2 항에 기재된 조성을 갖는 강편을 열간 압연 후, 2 ℃/s 이하의 냉각 속도로 400 ℃ 이하까지 냉각시키는 내마모 강판의 제조 방법.The manufacturing method of the wear resistant steel plate which cools the steel piece which has a composition of Claim 1 or 2 after hot rolling to 400 degrees C or less at the cooling rate of 2 degrees C / s or less. 제 5 항에 있어서,6. The method of claim 5, 추가로, 열간 압연에서의, 920 ℃ 이하에서의 압하율을 30 ％ 이상으로 하고, 압연 종료 온도를 900 ℃ 이하로 하는 가공성이 우수한 내마모 강의 제조 방법.Furthermore, the manufacturing method of the wear-resistant steel excellent in the workability which makes the reduction ratio in 920 degreeC or less in hot rolling 30% or more, and makes rolling end temperature 900 degrees C or less.
KR1020097021902A 2007-05-29 2008-05-26 Abrasion-resistant steel sheet having excellent processability, and method for production thereof KR101165654B1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JPJP-P-2007-142003 2007-05-29
JP2007142003 2007-05-29
JP2008113529A JP5380892B2 (en) 2007-05-29 2008-04-24 Wear-resistant steel plate with excellent workability and method for producing the same
JPJP-P-2008-113529 2008-04-24
PCT/JP2008/060096 WO2008146929A1 (en) 2007-05-29 2008-05-26 Abrasion-resistant steel sheet having excellent processability, and method for production thereof

Publications (2)

Publication Number Publication Date
KR20090123006A KR20090123006A (en) 2009-12-01
KR101165654B1 true KR101165654B1 (en) 2012-07-16

Family

ID=40075158

Family Applications (1)

Application Number Title Priority Date Filing Date
KR1020097021902A KR101165654B1 (en) 2007-05-29 2008-05-26 Abrasion-resistant steel sheet having excellent processability, and method for production thereof

Country Status (12)

Country Link
US (1) US20100147424A1 (en)
EP (1) EP2154262B1 (en)
JP (1) JP5380892B2 (en)
KR (1) KR101165654B1 (en)
CN (1) CN101688283B (en)
AU (1) AU2008255706B2 (en)
BR (1) BRPI0812277A2 (en)
CA (1) CA2685710C (en)
CL (1) CL2008001542A1 (en)
MX (1) MX2009012820A (en)
PE (1) PE20090342A1 (en)
WO (1) WO2008146929A1 (en)

Families Citing this family (42)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5458624B2 (en) * 2009-03-25 2014-04-02 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent workability and method for producing the same
FR2960883B1 (en) * 2010-06-04 2012-07-13 Vallourec Mannesmann Oil & Gas LOW-ALLOY STEEL WITH HIGH ELASTICITY LIMIT AND HIGH STRENGTH RESISTANCE TO SULFIDE-CONTAMINATED CRACKING
KR101271781B1 (en) * 2010-12-23 2013-06-07 주식회사 포스코 Steel sheet for oil sands slurry transportation system having excellent wear resistance, corrosion resistance and low temperature toughness, and method for manufacturing the same
KR101253897B1 (en) * 2010-12-23 2013-04-16 주식회사 포스코 Steel sheet for oil sands slurry transportation system having excellent wear resistance and corrosion resistance and method for manufacturing the same
CN102296234A (en) * 2011-09-07 2011-12-28 柳州钢铁股份有限公司 Abrasion-resistant steel plate and production device and production method thereof
JP5375981B2 (en) * 2012-01-10 2013-12-25 Ｊｆｅスチール株式会社 Wear-resistant welded steel pipe with excellent weld crack resistance and method for producing the same
KR101382833B1 (en) * 2012-03-16 2014-04-08 주식회사 포스코 Steel sheet for oil sands slurry pipe having excellent erosion resistance and method for manufacturing the same
KR101382790B1 (en) * 2012-03-16 2014-04-08 주식회사 포스코 Steel sheet for oil sands slury pipe having excellent erosion resistance and low temperature toughness and method for manufacturing the same
KR101382675B1 (en) 2012-03-19 2014-04-07 주식회사 포스코 Low alloy hot-rolled steel sheet having excellent wear-resistant and workability and method for manufacturing the same
CN102876993A (en) * 2012-10-24 2013-01-16 章磊 High-strength corrosion-resisting steel material and manufacturing method thereof
KR101461741B1 (en) * 2012-12-21 2014-11-14 주식회사 포스코 Thick hot rolled steel plate for steel pipe and steel pipe produced therefrom having excellent impact toughness and method for manufacturing thereof
CN103898420A (en) * 2012-12-25 2014-07-02 隆英(金坛)特钢科技有限公司 Wear-resisting steel plate and manufacturing method thereof
CN103272851A (en) * 2013-05-20 2013-09-04 浙江朋诚科技有限公司 High-speed mill roller box
CN103272848B (en) * 2013-05-20 2015-12-02 浙江朋诚科技有限公司 A kind of fast mill roll shaft
CN103266270A (en) * 2013-05-23 2013-08-28 江苏久联冶金机械制造有限公司 Boron-containing iron-based wear-resistant material
CN103409695B (en) * 2013-08-16 2015-04-08 洛阳钢丰机械制造有限公司 Composite material pouring-casted bucket and its production technology and production device
CN103469077B (en) * 2013-09-30 2015-12-02 济钢集团有限公司 A kind of high silicon rolled sheet material and preparation technology thereof
CN104561823B (en) * 2013-10-09 2016-12-07 宝钢特钢有限公司 A kind of deep-draw superhigh intensity steel hot rolled steel plate and manufacture method
BR112016017304B1 (en) 2014-01-28 2021-01-05 Jfe Steel Corporation abrasion resistant steel plate and method for producing the same
CN103882331A (en) * 2014-02-25 2014-06-25 南通东方科技有限公司 High-strength and high-wear-resistant supporting wheel for large type excavator
KR101955839B1 (en) * 2014-10-17 2019-03-07 신닛테츠스미킨 카부시키카이샤 Rolled steel for cracked connecting rods
CN105779885B (en) * 2014-12-23 2018-03-27 上海梅山钢铁股份有限公司 A kind of wear-resistant hot rolling sheet metal and its manufacture method with excellent machinability
CN105018848A (en) * 2015-08-05 2015-11-04 启东市佳宝金属制品有限公司 Abrasion-resistant alloy
CN105063497B (en) * 2015-09-17 2017-10-17 东北大学 A kind of high-wear resistance easy processing low alloy wear resistance steel plate and its manufacture method
CN105349896B (en) * 2015-10-28 2017-03-22 安徽省三方新材料科技有限公司 Preparation method for low-alloy excavator bucket tooththereof
CN105220077B (en) * 2015-11-11 2017-05-10 武汉钢铁(集团)公司 High surface quality hot rolled steel plate for manufacturing excavator bucket and manufacturing method
CN105779895A (en) * 2016-04-22 2016-07-20 柳州凯通新材料科技有限公司 Manganese-tungsten-titanium wear-resisting cast steel and machining process thereof
CN105695878A (en) * 2016-04-22 2016-06-22 柳州凯通新材料科技有限公司 Manganese-tungsten-titanium wear-resistant cast steel and preparation method thereof
CN105671438B (en) * 2016-04-22 2018-06-29 柳州凯通新材料科技有限公司 A kind of manganese-tungsten-titanium alloy steel and its processing technology
CN105695861B (en) * 2016-04-22 2018-04-24 柳州凯通新材料科技有限公司 A kind of wear-resisting Rolling compund steel plate
CN108034940B (en) * 2017-11-24 2020-08-25 宁波祥福机械科技有限公司 Turbine supercharging rotor shaft and preparation method thereof
CN108588573A (en) * 2018-04-28 2018-09-28 江苏恒加机械工程有限公司 A kind of production technology of metallic support
CN109881120A (en) * 2019-03-15 2019-06-14 重庆明高机械制造有限公司 A kind of husky bucket of digging
CN110387499A (en) * 2019-06-27 2019-10-29 扬州市海纳源科技服务有限责任公司 It is a kind of to mix low-alloyed metal material and preparation method
CN112442635B (en) * 2020-11-13 2022-03-29 唐山钢铁集团高强汽车板有限公司 High-performance low-alloy high-strength steel plate with strength of above 800MPa and preparation method thereof
CN112553543A (en) * 2020-11-30 2021-03-26 攀钢集团研究院有限公司 Bainite-based wear-resistant steel and production method thereof
CN112813362B (en) * 2020-12-14 2023-03-28 内蒙古科技大学 Manufacturing method of high-strength steel and high-strength steel track shoe
CN114774799B (en) * 2022-03-02 2023-04-18 河钢乐亭钢铁有限公司 Wear-resistant round bar for agricultural machinery and production method thereof
CN114737136B (en) * 2022-03-30 2023-05-16 鞍钢股份有限公司 Production method of high-strength high-toughness hot continuous rolling thin steel plate with Brinell hardness of 400HBW
CN115612923B (en) * 2022-09-13 2023-11-14 攀钢集团攀枝花钢铁研究院有限公司 Wear-resistant steel with good forming and welding performances and production method thereof
CN115558864B (en) * 2022-10-19 2023-10-24 湖南华菱涟源钢铁有限公司 High-strength steel plate and preparation method thereof
CN115838897A (en) * 2022-11-18 2023-03-24 莱芜钢铁集团银山型钢有限公司 Martensite wear-resistant corrosion-resistant steel pipe for 415 HB-level sediment conveying pipeline and preparation method thereof

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62142726A (en) 1985-12-18 1987-06-26 Kobe Steel Ltd Manufacture of wear resistant steel sheet having satisfactory weldability
JPS63169359A (en) 1986-12-29 1988-07-13 Sumitomo Metal Ind Ltd Thick steel plate having high toughness and wear resistance
JPH01142023A (en) 1987-11-30 1989-06-02 Kobe Steel Ltd Manufacture of wear-resistant steel plate having superior bendability
JPH0441616A (en) * 1990-06-06 1992-02-12 Nkk Corp Production of low-hardness water-resistant steel excellent in wear resistance and bendability
JPH04228536A (en) * 1990-06-06 1992-08-18 Nkk Corp Steel excellent in wear resistance
US5284529A (en) * 1990-06-06 1994-02-08 Nkk Corporation Abrasion-resistant steel
JPH0834684B2 (en) * 1990-11-30 1996-03-29 財団法人鉄道総合技術研究所 Magnetic levitation vehicle propulsion device
JP3089882B2 (en) * 1993-03-09 2000-09-18 日本鋼管株式会社 Abrasion-resistant steel having excellent surface properties and method for producing the same
JPH04308058A (en) * 1991-04-02 1992-10-30 Nkk Corp Steel having superior wear resistance
JPH05239591A (en) * 1992-02-27 1993-09-17 Nkk Corp Steel excellent in wear resistance
JP4239257B2 (en) * 1998-11-02 2009-03-18 Ｊｆｅスチール株式会社 Method for producing Ti-containing ferritic stainless steel sheet having excellent ridging resistance
JP3940301B2 (en) * 2002-02-27 2007-07-04 新日本製鐵株式会社 Blasting weathering high-strength steel plate with excellent bending resistance and method for producing the same
FR2847272B1 (en) * 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET
JP4257539B2 (en) * 2003-09-01 2009-04-22 住友金属工業株式会社 Non-tempered steel for soft nitriding
JP5017937B2 (en) * 2005-12-28 2012-09-05 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent bending workability
JP4899874B2 (en) * 2007-01-12 2012-03-21 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent workability and method for producing the same

Also Published As

Publication number Publication date
EP2154262A1 (en) 2010-02-17
CN101688283B (en) 2012-02-01
EP2154262A4 (en) 2016-01-20
AU2008255706B2 (en) 2011-10-13
CL2008001542A1 (en) 2008-09-05
MX2009012820A (en) 2009-12-15
WO2008146929A9 (en) 2009-11-12
JP2009007665A (en) 2009-01-15
CA2685710C (en) 2012-07-31
EP2154262B1 (en) 2018-03-07
US20100147424A1 (en) 2010-06-17
PE20090342A1 (en) 2009-03-29
AU2008255706A1 (en) 2008-12-04
CA2685710A1 (en) 2008-12-04
JP5380892B2 (en) 2014-01-08
WO2008146929A1 (en) 2008-12-04
KR20090123006A (en) 2009-12-01
CN101688283A (en) 2010-03-31
BRPI0812277A2 (en) 2014-11-18

Similar Documents

Publication Publication Date Title
KR101165654B1 (en) Abrasion-resistant steel sheet having excellent processability, and method for production thereof
KR102250916B1 (en) Abrasion-resistant steel plate and method of manufacturing same
JP5186809B2 (en) Wear-resistant steel plate with excellent workability and method for producing the same
RU2674796C2 (en) High-hardness hot-rolled steel product and method of manufacturing same
CN110100034B (en) High-hardness wear-resistant steel and method for manufacturing same
JP4735167B2 (en) Method for producing wear-resistant steel sheet with excellent low-temperature toughness
JP4650013B2 (en) Abrasion resistant steel plate with excellent low temperature toughness and method for producing the same
CN102392186B (en) Manufacturing method of HB500 grade low-manganese wear-resistant steel plate
JP4899874B2 (en) Wear-resistant steel plate with excellent workability and method for producing the same
KR101033711B1 (en) Wear-resistant steel sheet having excellent wear resistance at high temperatures and excellent bending workability and method for manufacturing the same
JP4238832B2 (en) Abrasion-resistant steel plate and method for producing the same
JP6540764B2 (en) Wear-resistant steel plate and method of manufacturing the same
JP7163888B2 (en) Manufacturing method for wear-resistant steel with excellent fatigue resistance
JP5458624B2 (en) Wear-resistant steel plate with excellent workability and method for producing the same
JP2011179122A (en) Wear-resistant steel sheet excellent in low temperature toughness
CN114729435A (en) High-hardness wear-resistant steel with excellent low-temperature impact toughness and manufacturing method thereof
JP5217191B2 (en) Wear-resistant steel plate with excellent workability and method for producing the same
JP5348392B2 (en) Wear resistant steel
JP5017937B2 (en) Wear-resistant steel plate with excellent bending workability
KR102031443B1 (en) Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same
JP4894296B2 (en) Wear-resistant steel plate
JP4894297B2 (en) Wear-resistant steel plate
JP4645306B2 (en) Wear-resistant steel with excellent low-temperature toughness and method for producing the same
JP6791179B2 (en) Non-microalloyed steel and its manufacturing method
JP7063420B1 (en) Manufacturing method of wear-resistant steel sheet and wear-resistant steel sheet

Legal Events

Date Code Title Description
A201 Request for examination
E701 Decision to grant or registration of patent right
GRNT Written decision to grant
FPAY Annual fee payment

Payment date: 20150618

Year of fee payment: 4

FPAY Annual fee payment

Payment date: 20160616

Year of fee payment: 5

FPAY Annual fee payment

Payment date: 20170616

Year of fee payment: 6

FPAY Annual fee payment

Payment date: 20190617

Year of fee payment: 8