KR20240098230A - Wear resistant steel havinh high hardness and method for manufacturing the same - Google Patents
Wear resistant steel havinh high hardness and method for manufacturing the same Download PDFInfo
- Publication number
- KR20240098230A KR20240098230A KR1020220179266A KR20220179266A KR20240098230A KR 20240098230 A KR20240098230 A KR 20240098230A KR 1020220179266 A KR1020220179266 A KR 1020220179266A KR 20220179266 A KR20220179266 A KR 20220179266A KR 20240098230 A KR20240098230 A KR 20240098230A
- Authority
- KR
- South Korea
- Prior art keywords
- less
- excluding
- steel
- hardness
- resistant steel
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 104
- 239000010959 steel Substances 0.000 title claims abstract description 104
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 title claims description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 24
- 239000010936 titanium Substances 0.000 claims abstract description 20
- 239000010949 copper Substances 0.000 claims abstract description 19
- 239000010955 niobium Substances 0.000 claims abstract description 19
- 239000011575 calcium Substances 0.000 claims abstract description 18
- 239000011651 chromium Substances 0.000 claims abstract description 18
- 239000011572 manganese Substances 0.000 claims abstract description 17
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 13
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 8
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 8
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 7
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 7
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 7
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 7
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 239000011733 molybdenum Substances 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 239000011574 phosphorus Substances 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 239000010703 silicon Substances 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 239000011593 sulfur Substances 0.000 claims abstract description 7
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 6
- 239000010941 cobalt Substances 0.000 claims abstract description 6
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 6
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 6
- 238000001816 cooling Methods 0.000 claims description 26
- 238000003303 reheating Methods 0.000 claims description 17
- 238000005096 rolling process Methods 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 14
- 229910052718 tin Inorganic materials 0.000 claims description 7
- 229910052721 tungsten Inorganic materials 0.000 claims description 6
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 5
- 229910052785 arsenic Inorganic materials 0.000 claims description 5
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 4
- 239000010937 tungsten Substances 0.000 claims description 4
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims description 3
- 230000000694 effects Effects 0.000 description 11
- 238000005520 cutting process Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- 229910001566 austenite Inorganic materials 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005530 etching Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- AWFYPPSBLUWMFQ-UHFFFAOYSA-N 2-[5-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-1,3,4-oxadiazol-2-yl]-1-(1,4,6,7-tetrahydropyrazolo[4,3-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1=NN=C(O1)CC(=O)N1CC2=C(CC1)NN=C2 AWFYPPSBLUWMFQ-UHFFFAOYSA-N 0.000 description 1
- NIPNSKYNPDTRPC-UHFFFAOYSA-N N-[2-oxo-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 NIPNSKYNPDTRPC-UHFFFAOYSA-N 0.000 description 1
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 1
- 229910001035 Soft ferrite Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000004568 cement Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
-
- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- 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
- C21D2211/008—Martensite
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)
Abstract
심부경도가 우수한 고경도 내마모강판 및 그 제조방법이 제공된다.
본 발명의 내마모강판은, 중량%로, 탄소(C): 0.19~0.32%, 실리콘(Si): 0.1~0.7%, 망간(Mn): 0.6~1.6%, 인(P): 0.05% 이하(0은 제외), 황(S): 0.02% 이하(0은 제외), 알루미늄(Al): 0.07% 이하(0은 제외), 크롬(Cr): 0.1~1.5%, 니켈(Ni): 0.01~2.0%, 몰리브덴(Mo): 0.01~0.8%, 보론(B): 50ppm 이하(0은 제외), 코발트(Co): 0.04% 이하을 포함하고, 구리(Cu): 0.5% 이하(0은 제외), 티타늄(Ti): 0.04% 이하(0은 제외), 니오븀(Nb): 0.05% 이하(0은 제외), 바나듐(V): 0.05% 이하(0은 제외) 및 칼슘(Ca): 2~100ppm 중 1종 이상을 더 포함하고, 잔부 Fe 및 기타 불가피한 불순물을 포함하며, 미세조직이 면적분율 85% 이상의 마르텐사이트, 10% 이하의 베이나이트, 잔여 페라이트를 포함한다. A high-hardness wear-resistant steel sheet with excellent core hardness and a manufacturing method thereof are provided.
The wear-resistant steel sheet of the present invention contains, in weight percent, carbon (C): 0.19 to 0.32%, silicon (Si): 0.1 to 0.7%, manganese (Mn): 0.6 to 1.6%, phosphorus (P): 0.05% or less. (excluding 0), Sulfur (S): 0.02% or less (excluding 0), Aluminum (Al): 0.07% or less (excluding 0), Chromium (Cr): 0.1 to 1.5%, Nickel (Ni): 0.01 ~2.0%, molybdenum (Mo): 0.01~0.8%, boron (B): 50ppm or less (excluding 0), cobalt (Co): including 0.04% or less, copper (Cu): 0.5% or less (excluding 0) ), Titanium (Ti): 0.04% or less (excluding 0), Niobium (Nb): 0.05% or less (excluding 0), Vanadium (V): 0.05% or less (excluding 0), and Calcium (Ca): 2 It further contains one or more of ~100 ppm, contains the balance Fe and other inevitable impurities, and has a microstructure of martensite with an area fraction of 85% or more, bainite with an area fraction of 10% or less, and residual ferrite.
Description
본 발명은 심부경도가 우수한 고경도 내마모강판 제조에 관한 것으로, 보다 상세하게는, 건설 중장비用 Bucket 보강재(Cutting Edges)로 주로 적용되고 있는 심부경도가 우수한 HB500급 내마모강판 및 그 제조방법에 관한 것이다.The present invention relates to the manufacture of high-hardness wear-resistant steel sheets with excellent core hardness, and more specifically, to the HB500 class wear-resistant steel sheets with excellent core hardness, which are mainly applied as bucket reinforcements (cutting edges) for heavy construction equipment, and their manufacturing method. It's about.
건설, 토목, 광산업, 시멘트 산업 등 많은 산업분야에 사용되는 건설기계, 산업기계들의 경우 작업시 마찰에 의한 마모가 심하게 발생됨에 따라 내마모의 특성을 나타내는 소재의 적용이 필요하다.In the case of construction machinery and industrial machinery used in many industrial fields such as construction, civil engineering, mining, and cement industries, severe wear due to friction occurs during work, so it is necessary to apply materials that exhibit wear resistance characteristics.
일반적으로, 후강판의 내마모성과 경도는 상관이 있어, 마모가 염려되는 후강판에서는 경도를 높일 필요가 있다. 보다 안정적인 내마모성을 확보하기 위해서는, 후강판의 표면으로부터 판 두께 내부(t/2 근방, t = 두께)에 걸쳐 균일한 경도를 갖는 것(즉, 후강판의 표면과 내부에서 동일한 정도의 경도를 갖는 것)이 요구된다.In general, the wear resistance and hardness of thick steel plates are correlated, and it is necessary to increase the hardness of thick steel plates where wear is a concern. In order to ensure more stable wear resistance, it is necessary to have uniform hardness from the surface of the thick steel plate to the inside of the plate thickness (near t/2, t = thickness) (i.e., to have the same degree of hardness on the surface and inside the thick steel plate). ) is required.
HB500급 고경도 내마모강의 경우, Ceq(탄소당량)가 높아 가스절단 시, 절단면의 저온균열이 발생이 빈번하고, 이를 억제하기 위해 일정온도의 예열이 필수적으로 선행되어야한다. In the case of HB500 grade high hardness wear-resistant steel, Ceq (carbon equivalent) is high, so low-temperature cracks on the cutting surface frequently occur during gas cutting, and preheating to a certain temperature must be carried out in advance to suppress this.
예열 공정은 제품 생산성을 낮추며, 원가를 상승시키기도 하지만, 예열에 의한 내마모 강판의 연화 현상이 발생하여, 경도하락을 초래한다. 뿐만 아니라 중장비 내마모 강판은 일반적으로 가스절단 공정으로 부품 제작이 이루어지는데, 절단 과정에서 절단열에 기인한 재질열화로 인해 열영향부의 경도 하락이 발생한다. The preheating process lowers product productivity and increases costs, but also causes softening of the wear-resistant steel sheet due to preheating, resulting in a decrease in hardness. In addition, heavy equipment wear-resistant steel plates are generally manufactured through a gas cutting process, and the hardness of the heat-affected zone decreases due to material deterioration due to cutting heat during the cutting process.
이러한 내마모강판의 경도 하락은 내마모 성능 등의 품질저하 문제로 직결되기 때문에 내마모강판의 절단 및 면취가공 후에도 고경도 성능을 유지하는 것은 매우 중요하다. Since this decline in hardness of wear-resistant steel sheets is directly linked to quality deterioration issues such as wear-resistant performance, it is very important to maintain high hardness performance even after cutting and chamfering of wear-resistant steel sheets.
본 발명은 고경도 내마모강을 활용하여 제작되는 내마모 부품(Cutting edge, lip plate)의 절단면 저온균열 및 절단부 경도하락을 방지할 수 있는 내마모강 및 그 제조방법을 제공함을 목적으로 한다. The purpose of the present invention is to provide a wear-resistant steel and a manufacturing method thereof that can prevent low-temperature cracking and a decrease in hardness of the cut surface of wear-resistant parts (cutting edge, lip plate) manufactured using high-hardness wear-resistant steel.
또한 본 발명에서 이루고자 하는 기술적 과제들은 이상에서 언급한 기술적 과제들에 한정되지 않으며, 언급하지 않은 또 다른 기술적 과제들은 아래의 기재로부터 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자에게 명확하게 이해될 수 있을 것이다.In addition, the technical problems to be achieved in the present invention are not limited to the technical problems mentioned above, and other technical problems not mentioned can be clearly understood by those skilled in the art from the description below. It could be.
본 발명의 일측 면은, One aspect of the present invention is,
중량%로, 탄소(C): 0.19~0.32%, 실리콘(Si): 0.1~0.7%, 망간(Mn): 0.6~1.6%, 인(P): 0.05% 이하(0은 제외), 황(S): 0.02% 이하(0은 제외), 알루미늄(Al): 0.07% 이하(0은 제외), 크롬(Cr): 0.1~1.5%, 니켈(Ni): 0.01~2.0%, 몰리브덴(Mo): 0.01~0.8%, 보론(B): 50ppm 이하(0은 제외), 코발트(Co): 0.04% 이하을 포함하고, 구리(Cu): 0.5% 이하(0은 제외), 티타늄(Ti): 0.04% 이하(0은 제외), 니오븀(Nb): 0.05% 이하(0은 제외), 바나듐(V): 0.05% 이하(0은 제외) 및 칼슘(Ca): 2~100ppm 중 1종 이상을 더 포함하고, 잔부 Fe 및 기타 불가피한 불순물을 포함하며, 미세조직이 면적분율 85% 이상의 마르텐사이트, 10% 이하의 베이나이트, 잔여 페라이트를 포함하는 고경도 내마모강에 관한 것이다.In weight percent, carbon (C): 0.19~0.32%, silicon (Si): 0.1~0.7%, manganese (Mn): 0.6~1.6%, phosphorus (P): 0.05% or less (excluding 0), sulfur ( S): 0.02% or less (excluding 0), Aluminum (Al): 0.07% or less (excluding 0), Chromium (Cr): 0.1 to 1.5%, Nickel (Ni): 0.01 to 2.0%, Molybdenum (Mo) : 0.01~0.8%, Boron (B): 50ppm or less (excluding 0), Cobalt (Co): Contains 0.04% or less, Copper (Cu): 0.5% or less (excluding 0), Titanium (Ti): 0.04 % or less (excluding 0), Niobium (Nb): 0.05% or less (excluding 0), Vanadium (V): 0.05% or less (excluding 0), and Calcium (Ca): one or more of 2 to 100 ppm. It relates to a high-hardness wear-resistant steel containing the balance Fe and other inevitable impurities, and whose microstructure includes martensite with an area fraction of 85% or more, bainite with an area fraction of 10% or less, and residual ferrite.
또한 본 발명의 다른 측면은, In addition, another aspect of the present invention is,
상술한 합금조성을 만족하는 강 슬라브를 준비하는 단계; Preparing a steel slab satisfying the above-described alloy composition;
상기 강 슬라브를 1050~1250℃의 온도범위에서 가열하는 단계; Heating the steel slab at a temperature range of 1050 to 1250°C;
상기 재가열된 강 슬라브를 950~1050℃의 온도범위에서 조압연하는 단계; 상기 조압연 후 750~950℃의 온도범위에서 마무리 압연하여 열연강판을 제조하는 단계; Rough rolling the reheated steel slab at a temperature range of 950 to 1050°C; Manufacturing a hot-rolled steel sheet by performing finish rolling at a temperature range of 750 to 950° C. after the rough rolling;
상기 열연강판을 상온까지 공냉 후, 850~950℃의 온도범위에서 재로시간 20분 이상으로 재가열 열처리하는 단계; 및 Air-cooling the hot-rolled steel sheet to room temperature and then reheating and heat-treating the hot-rolled steel sheet at a temperature range of 850 to 950°C for a reheat time of 20 minutes or more; and
상기 재가열 열처리 후 상기 열연강판을 9.0℃/s 이상의 냉각속도로 200℃ 이하까지 냉각하는 단계를 포함하는 고경도 내마모강의 제조방법에 관한 것이다. It relates to a method of manufacturing high hardness wear-resistant steel including the step of cooling the hot rolled steel sheet to 200°C or less at a cooling rate of 9.0°C/s or more after the reheating heat treatment.
상술한 구성의 본 발명에 의하면, 고경도 내마모강판의 절단면 저온균열이 발생하지 않으며, 절단면 열영향부의 경도가 하락하는 현상이 최소화될 수 있다. 또한 중심부의 경우, 기존 시장에서 활용되고 있는 타사 제품에 비해 월등히 높은 경도를 확보할 수 있다. According to the present invention of the above-described configuration, low-temperature cracks do not occur at the cut surface of the high-hardness wear-resistant steel sheet, and the phenomenon of a decrease in hardness of the heat-affected zone at the cut surface can be minimized. In addition, in the case of the center, it is possible to secure much higher hardness than other products used in the existing market.
도 1은 본 발명의 일실시예 따른 냉각속도와 비커스 경도와의 상관관계를 보여주는 그림이다.
도 2는 본 발명의 일실시예에 따른 재가열온도와 열연강판의 브리넬 경도와의 상관관계를 보여주는 그림이다.
도 3은 본 발명에 따른 개발재의 강판 두께에 따른 경도 프로파일을 종래재와 대비하여 나타낸 그림이다. Figure 1 is a diagram showing the correlation between cooling rate and Vickers hardness according to an embodiment of the present invention.
Figure 2 is a diagram showing the correlation between reheating temperature and Brinell hardness of a hot rolled steel sheet according to an embodiment of the present invention.
Figure 3 is a diagram showing the hardness profile according to the steel plate thickness of the developed material according to the present invention compared to the conventional material.
이하, 본 발명에 대하여 상세히 설명한다.Hereinafter, the present invention will be described in detail.
본 발명의 일 측면에 따른 고경도 내마모강은, 중량%로, 탄소(C): 0.19~0.32%, 실리콘(Si): 0.1~0.7%, 망간(Mn): 0.6~1.6%, 인(P): 0.05% 이하(0은 제외), 황(S): 0.02% 이하(0은 제외), 알루미늄(Al): 0.07% 이하(0은 제외), 크롬(Cr): 0.1~1.5%, 니켈(Ni): 0.01~2.0%, 몰리브덴(Mo): 0.01~0.8%, 보론(B): 50ppm 이하(0은 제외), 코발트(Co): 0.04% 이하을 포함하고, 구리(Cu): 0.5% 이하(0은 제외), 티타늄(Ti): 0.04% 이하(0은 제외), 니오븀(Nb): 0.05% 이하(0은 제외), 바나듐(V): 0.05% 이하(0은 제외) 및 칼슘(Ca): 2~100ppm 중 1종 이상을 더 포함하고, 잔부 Fe 및 기타 불가피한 불순물을 포함하는 것이 바람직하다. The high hardness wear-resistant steel according to one aspect of the present invention contains, in weight percent, carbon (C): 0.19 to 0.32%, silicon (Si): 0.1 to 0.7%, manganese (Mn): 0.6 to 1.6%, phosphorus ( P): 0.05% or less (excluding 0), Sulfur (S): 0.02% or less (excluding 0), Aluminum (Al): 0.07% or less (excluding 0), Chromium (Cr): 0.1 to 1.5%, Nickel (Ni): 0.01 to 2.0%, molybdenum (Mo): 0.01 to 0.8%, boron (B): 50 ppm or less (excluding 0), cobalt (Co): 0.04% or less, copper (Cu): 0.5 % or less (excluding 0), Titanium (Ti): 0.04% or less (excluding 0), Niobium (Nb): 0.05% or less (excluding 0), Vanadium (V): 0.05% or less (excluding 0), and Calcium (Ca): It is preferable to further include at least one type from 2 to 100 ppm, and to include the remainder of Fe and other unavoidable impurities.
이하에서는 본 발명에서 제공하는 고경도 내마모강의 합금조성을 위와 같이 제어한 이유에 대하여 상세히 설명한다. 이때, 특별한 언급이 없는 한, 각 성분의 함량은 중량%를 의미한다.Hereinafter, the reason for controlling the alloy composition of the high hardness wear-resistant steel provided by the present invention as described above will be explained in detail. At this time, unless otherwise specified, the content of each ingredient refers to weight percent.
C: 0.19~0.32%C: 0.19~0.32%
탄소(C)는 마르텐사이트 조직을 갖는 강에서 강도와 경도를 증가시키는데 효과적이며 경화능 향상을 위하여 유효한 원소이다.Carbon (C) is effective in increasing the strength and hardness of steel with a martensitic structure and is an effective element for improving hardenability.
상술한 효과를 충분히 확보하기 위해서는 0.19% 이상으로 C를 첨가하는 것이 바람직하나, 만일 그 함량이 0.32%를 초과하게 되면 용접성 및 인성을 저해하는 문제가 있다.In order to sufficiently secure the above-mentioned effects, it is desirable to add C in an amount of 0.19% or more, but if the content exceeds 0.32%, there is a problem of impairing weldability and toughness.
따라서, 본 발명에서는 상기 C의 함량을 0.19~0.32%로 제어하는 것이 바람직하다. 보다 바람직하게는, 0.19~0.30% 범위로 제어하는 것이다. Therefore, in the present invention, it is preferable to control the C content to 0.19 to 0.32%. More preferably, it is controlled in the range of 0.19 to 0.30%.
Si: 0.1~0.7%Si: 0.1~0.7%
실리콘(Si)은 탈산과 고용강화에 따른 강도 향상에 유효한 원소이다. Silicon (Si) is an element effective in improving strength through deoxidation and solid solution strengthening.
위와 같은 효과를 유효하기 얻기 위해서는 0.1% 이상으로 Si을 첨가하는 것이 바람직하나, 그 함량이 0.7%를 초과하게 되면 용접성이 열화되므로 바람직하지 못하다.In order to effectively obtain the above effect, it is preferable to add Si in an amount of 0.1% or more, but if the content exceeds 0.7%, weldability deteriorates, so it is not preferable.
따라서, 본 발명에서는 상기 Si의 함량을 0.1~0.7%로 제어하는 것이 바람직하다.Therefore, in the present invention, it is preferable to control the Si content to 0.1 to 0.7%.
Mn: 0.6~1.6%Mn: 0.6~1.6%
망간(Mn)은 페라이트 생성을 억제하고, Ar3 온도를 낮춤으로써 소입성을 효과적으로 상승시켜 강의 강도 및 인성을 향상시키는 원소이다.Manganese (Mn) is an element that improves the strength and toughness of steel by suppressing the formation of ferrite and effectively increasing hardenability by lowering the Ar3 temperature.
본 발명에서는 후물재의 경도 확보를 위해서는 상기 Mn을 0.6% 이상으로 함유하는 것이 바람직하나, 그 함량이 1.6%를 초과하게 되면 용접성을 저하시키는 문제가 있다.In the present invention, in order to secure the hardness of the thick material, it is preferable to contain Mn in an amount of 0.6% or more, but if the content exceeds 1.6%, there is a problem of deteriorating weldability.
따라서, 본 발명에서는 상기 Mn의 함량을 0.6~1.6%로 제어하는 것이 바람직하다.Therefore, in the present invention, it is preferable to control the Mn content to 0.6 to 1.6%.
P: 0.05% 이하P: 0.05% or less
인(P)은 강 중 불가피하게 함유되는 원소이면서, 강의 인성을 저해하는 원소이다. 따라서, 상기 P의 함량을 가능한 한 낮추어서 0.05% 이하로 제어하는 것이 바람직하며, 다만 불가피하게 함유되는 수준을 고려하여 0%는 제외한다.Phosphorus (P) is an element that is inevitably contained in steel, and is an element that inhibits the toughness of steel. Therefore, it is desirable to control the content of P as low as possible to 0.05% or less, but 0% is excluded in consideration of the unavoidable content level.
S: 0.02% 이하S: 0.02% or less
황(S)은 강 중 MnS 개재물을 형성하여 강의 인성을 저해하는 원소이다. 따라서, 상기 S의 함량을 가능한 한 낮추어서 0.02% 이하로 제어하는 것이 바람직하며, 다만 불가피하게 함유되는 수준을 고려하여 0%는 제외한다.Sulfur (S) is an element that inhibits the toughness of steel by forming MnS inclusions in steel. Therefore, it is desirable to control the S content as low as possible to 0.02% or less, but considering the unavoidable content level, 0% is excluded.
Al: 0.07% 이하(0은 제외)Al: 0.07% or less (excluding 0)
알루미늄(Al)은 강의 탈산제로서 용강 중에 산소 함량을 낮추는데 효과적인 원소이다. 이러한 Al의 함량이 0.07%를 초과하게 되면 강의 청정성이 저해되는 문제가 있으므로 바람직하지 못하다.Aluminum (Al) is a deoxidizing agent for steel and is an effective element in lowering the oxygen content in molten steel. If the Al content exceeds 0.07%, it is undesirable because the cleanliness of the steel is impaired.
따라서, 본 발명에서는 상기 Al의 함량을 0.07% 이하로 제어하는 것이 바람직하며, 제강공정시 부하, 제조비용의 상승 등을 고려하여 0%는 제외한다.Therefore, in the present invention, it is preferable to control the Al content to 0.07% or less, and 0% is excluded in consideration of the load during the steelmaking process and increase in manufacturing cost.
Cr: 0.1~1.5%Cr: 0.1~1.5%
크롬(Cr)은 소입성을 증가시켜 강의 강도를 증가시키며, 경도 확보에도 유리한 원소이다.Chromium (Cr) increases the strength of steel by increasing hardenability and is an element that is advantageous in securing hardness.
상술한 효과를 위해서는 0.1% 이상으로 Cr을 첨가하는 것이 바람직하나, 그 함량이 1.5%를 초과하게 되면 용접성이 열위하며 제조원가를 상승시키는 원인이 된다.For the above-mentioned effect, it is preferable to add Cr in an amount of 0.1% or more, but if the content exceeds 1.5%, weldability is inferior and manufacturing costs increase.
따라서, 본 발명에서는 상기 Cr의 함량을 0.1~1.5%로 제어하는 것이 바람직하다.Therefore, in the present invention, it is preferable to control the Cr content to 0.1 to 1.5%.
Ni: 0.01~2.0%Ni: 0.01~2.0%
니켈(Ni)은 상기 Cr과 함께 소입성을 증가시켜 강의 강도와 더불어 인성을 향상시키는데에 유효한 원소이다.Nickel (Ni), together with Cr, is an element effective in improving toughness as well as strength of steel by increasing hardenability.
상술한 효과를 위해서는 0.01% 이상으로 Ni을 첨가하는 것이 바람직하나, 그 함량이 2.0%를 초과하게 되면 오히려 강의 인성을 크게 해칠 우려가 있으며, 고가의 원소로 제조원가를 상승시키는 원인이 된다.For the above-mentioned effect, it is preferable to add Ni in an amount of 0.01% or more, but if the content exceeds 2.0%, there is a risk of greatly damaging the toughness of the steel, and it is an expensive element, causing an increase in manufacturing costs.
따라서, 본 발명에서는 상기 Ni의 함량을 0.01~2.0%로 제어하는 것이 바람직하다.Therefore, in the present invention, it is preferable to control the Ni content to 0.01 to 2.0%.
Mo: 0.01~0.8%Mo: 0.01~0.8%
몰리브덴(Mo)은 강의 소입성을 증가시키며, 특히 후물재의 경도 향상에 유효한 원소이다.Molybdenum (Mo) increases the hardenability of steel and is an especially effective element in improving the hardness of thick materials.
상술한 효과를 충분히 얻기 위해서는 0.01% 이상으로 Mo을 첨가하는 것이 바람직하나, 상기 Mo 역시 고가의 원소로서 그 함량이 0.8%를 초과하게 되면 제조원가가 상승할 뿐만 아니라, 용접성이 열위하게 되는 문제가 있다.In order to sufficiently obtain the above-mentioned effect, it is preferable to add Mo in an amount of 0.01% or more. However, Mo is also an expensive element, and if its content exceeds 0.8%, not only does the manufacturing cost increase, but there is a problem in that weldability is inferior. .
따라서, 본 발명에서는 상기 Mo의 함량을 0.01~0.8%로 제어하는 것이 바람직하다.Therefore, in the present invention, it is preferable to control the Mo content to 0.01 to 0.8%.
B: 50ppm 이하(0은 제외)B: 50 ppm or less (excluding 0)
보론(B)은 소량의 첨가로도 강의 소입성을 유효하게 상승시켜 강도를 향상시키는데에 유효한 원소이다. Boron (B) is an element that is effective in improving strength by effectively increasing the hardenability of steel even with a small amount of addition.
다만, 그 함량이 과도하면 오히려 강의 인성 및 용접성을 저해하는 문제가 있으므로, 그 함량을 50ppm 이하로 제어하는 것이 바람직하며, 0%는 제외한다.However, if the content is excessive, there is a problem of impairing the toughness and weldability of the steel, so it is desirable to control the content to 50ppm or less, excluding 0%.
Co: 0.04% 이하(0 포함)Co: 0.04% or less (including 0)
코발트(Co)는 강의 소입성을 증가시킴으로써, 강의 강도와 더불어 경도 확보에 유리한 원소이다.Cobalt (Co) is an element that is advantageous in securing hardness as well as strength of steel by increasing the hardenability of steel.
다만, 그 함량이 0.04%를 초과하게 되면 강의 소입성이 저하될 우려가 있으며, 고가의 원소로 제조원가를 상승시키는 요인이 된다.However, if the content exceeds 0.04%, there is a risk that the hardenability of the steel may decrease, and it is an expensive element, which increases manufacturing costs.
따라서, 본 발명에서는 0.04% 이하로 Co를 첨가하는 것이 바람직하며, 보다 유리하게는 0.005~0.035%, 보다 더 유리하게는 0.01~0.03%로 함유하는 것이 바람직하다.Therefore, in the present invention, it is preferable to add Co at 0.04% or less, more advantageously at 0.005 to 0.035%, and even more advantageously at 0.01 to 0.03%.
본 발명의 내마모강은 상술한 합금조성 이외에도, 본 발명에서 목표로 하는 물성의 확보에 유리한 원소들을 더 포함할 수 있다.In addition to the alloy composition described above, the wear-resistant steel of the present invention may further contain elements advantageous for securing the physical properties targeted by the present invention.
구체적으로, 구리(Cu): 0.5% 이하(0은 제외), 티타늄(Ti): 0.02% 이하(0은 제외), 니오븀(Nb): 0.05% 이하(0은 제외), 바나듐(V): 0.05% 이하(0은 제외) 및 칼슘(Ca): 2~100ppm으로 이루어지는 그룹에서 선택된 1종 이상을 더 포함할 수 있다.Specifically, copper (Cu): 0.5% or less (excluding 0), titanium (Ti): 0.02% or less (excluding 0), niobium (Nb): 0.05% or less (excluding 0), vanadium (V): It may further include one or more selected from the group consisting of 0.05% or less (excluding 0) and calcium (Ca): 2 to 100 ppm.
Cu: 0.5% 이하(0은 제외)Cu: 0.5% or less (excluding 0)
구리(Cu)는 강의 소입성을 향상시키며, 고용강화로 강의 강도 및 경도를 향상시키는 원소이다.Copper (Cu) is an element that improves the hardenability of steel and improves the strength and hardness of steel through solid solution strengthening.
다만, 이러한 Cu의 함량이 0.5%를 초과하게 되면 표면결함을 발생시키며, 열간가공성을 저해하는 문제가 있으므로, 상기 Cu를 첨가하는 경우 0.5% 이하로 첨가하는 것이 바람직하다.However, if the Cu content exceeds 0.5%, surface defects may occur and hot workability may be impaired. Therefore, when adding Cu, it is preferable to add 0.5% or less.
Ti: 0.04% 이하(0은 제외)Ti: 0.04% or less (excluding 0)
티타늄(Ti)은 강의 소입성 향상에 유효한 원소인 B의 효과를 극대화하는 원소이다. 구체적으로, 상기 Ti은 질소(N)와 결합하여 TiN 석출물을 형성시켜 BN의 형성을 억제함으로써 고용 B를 증가시켜 소입성 향상을 극대화할 수 있다.Titanium (Ti) is an element that maximizes the effect of B, an element effective in improving the hardenability of steel. Specifically, the Ti combines with nitrogen (N) to form TiN precipitates to suppress the formation of BN, thereby increasing the solid solution B and maximizing the improvement of hardenability.
다만, 상기 Ti의 함량이 0.02%를 초과하게 되면 조대한 TiN 석출물이 형성되어 강의 인성이 열위하는 문제가 있다.However, if the Ti content exceeds 0.02%, coarse TiN precipitates are formed, which causes a problem in that the toughness of the steel is inferior.
따라서, 본 발명에서는 상기 Ti의 첨가시 0.04% 이하로 첨가하는 것이 바람직하다.Therefore, in the present invention, it is preferable to add Ti in an amount of 0.04% or less.
Nb: 0.05% 이하(0은 제외)Nb: 0.05% or less (excluding 0)
니오븀(Nb)은 오스테나이트에 고용되어 오스테나이트의 경화능을 증대시키고, Nb(C,N) 등의 탄질화물을 형성하여 강의 강도 증가 및 오스테나이트 결정립 성장을 억제하는데에 유효하다.Niobium (Nb) is dissolved in austenite to increase the hardenability of austenite, and is effective in increasing the strength of steel and suppressing austenite grain growth by forming carbonitrides such as Nb (C, N).
다만, 상기 Nb의 함량이 0.05%를 초과하게 되면 조대한 석출물이 형성되며, 이는 취성파괴의 기점이 되어 인성을 저해하는 문제가 있다.However, when the Nb content exceeds 0.05%, coarse precipitates are formed, which becomes the starting point of brittle fracture and reduces toughness.
따라서, 본 발명에서는 상기 Nb의 첨가시 0.05% 이하로 첨가하는 것이 바람직하다.Therefore, in the present invention, it is preferable to add 0.05% or less of Nb.
V: 0.05% 이하(0은 제외)V: 0.05% or less (excluding 0)
바나듐(V)은 열간압연 후 재가열시 VC 탄화물을 형성함으로써, 오스테나이트 결정립의 성장을 억제하고, 강의 소입성을 향상시켜 강도 및 인성을 확보하는데에 유리한 원소이다.Vanadium (V) is an element that is advantageous for securing strength and toughness by suppressing the growth of austenite grains and improving the hardenability of steel by forming VC carbides when reheated after hot rolling.
다만, 상기 V은 고가의 원소로 그 함량이 0.05%를 초과하게 되면 제조원가를 상승시키는 요인이 된다.However, V is an expensive element and if its content exceeds 0.05%, it becomes a factor that increases manufacturing costs.
따라서, 본 발명에서는 상기 V의 첨가시 그 함량을 0.05% 이하로 제어하는 것이 바람직하다.Therefore, in the present invention, when adding V, it is preferable to control the content to 0.05% or less.
Ca: 2~100ppmCa: 2~100ppm
칼슘(Ca)은 S과의 결합력이 좋아 CaS를 생성함으로써 강재 두께 중심부에 편석되는 MnS의 생성을 억제하는 효과가 있다. 또한, 상기 Ca의 첨가로 생성된 CaS는 다습한 외부 환경 하에서 부식 저항을 높이는 효과가 있다.Calcium (Ca) has a good bonding power with S, so it has the effect of suppressing the creation of MnS, which is segregated in the center of the steel thickness, by generating CaS. In addition, CaS produced by adding Ca has the effect of increasing corrosion resistance in a humid external environment.
상술한 효과를 위해서는 2ppm 이상으로 상기 Ca을 첨가하는 것이 바람직하나, 그 함량이 100ppm을 초과하게 되면 제강조업시 노즐 막힘 등을 유발하는 문제가 있으므로 바람직하지 못하다.For the above-mentioned effect, it is preferable to add Ca at more than 2ppm, but if the content exceeds 100ppm, it is not preferable because it may cause problems such as nozzle clogging during steelmaking operations.
따라서, 본 발명에서는 상기 Ca의 첨가시 그 함량을 2~100ppm으로 제어하는 것이 바람직하다.Therefore, in the present invention, when adding Ca, it is preferable to control the content to 2 to 100 ppm.
나아가, 본 발명은 비소(As): 0.05% 이하(0은 제외), 주석(Sn): 0.05% 이하(0은 제외) 및 텅스텐(W): 0.05% 이하(0은 제외) 중 1종 이상 더 포함할 수 있다.Furthermore, the present invention provides one or more of arsenic (As): 0.05% or less (excluding 0), tin (Sn): 0.05% or less (excluding 0), and tungsten (W): 0.05% or less (excluding 0). More may be included.
상기 As는 강의 인성 향상에 유효하며, 상기 Sn은 강의 강도 및 내식성 향상에 유효하다. 또한 W은 소입성을 증가시켜 강도 향상과 더불어 고온에서의 경도 향상에 유효한 원소이다.The As is effective in improving the toughness of steel, and the Sn is effective in improving the strength and corrosion resistance of the steel. In addition, W is an element that increases hardenability and is effective in improving strength and hardness at high temperatures.
다만, 상기 As, Sn 및 W의 함량이 각각 0.05%를 초과하게 되면 제조원가가 상승할 뿐만 아니라, 오히려 강의 물성을 해칠 우려가 있다.However, if the contents of As, Sn, and W each exceed 0.05%, not only does the manufacturing cost increase, but there is a risk that the physical properties of the steel may be harmed.
따라서, 본 발명에서는 상기 As, Sn 또는 W을 추가적으로 포함하는 경우, 그 함량을 각각 0.05% 이하로 제어하는 것이 바람직하다.Therefore, in the present invention, when As, Sn or W is additionally included, it is preferable to control the content to 0.05% or less.
본 발명의 나머지 성분은 철(Fe)이다. 다만, 통상의 제조과정에서는 원료 또는 주위 환경으로부터 의도되지 않는 불순물들이 불가피하게 혼입될 수 있으므로, 이를 배제할 수는 없다. 이들 불순물들은 통상의 제조과정의 기술자라면 누구라도 알 수 있는 것이기 때문에 그 모든 내용을 특별히 본 명세서에서 언급하지는 않는다.The remaining component of the present invention is iron (Fe). However, in the normal manufacturing process, unintended impurities from raw materials or the surrounding environment may inevitably be mixed, so this cannot be ruled out. Since these impurities are known to anyone skilled in the ordinary manufacturing process, all of them are not specifically mentioned in this specification.
상술한 합금조성을 만족하는 본 발명의 내마모강은 미세조직으로 마르텐사이트 상을 기지조직으로 포함하는 것이 바람직하다.The wear-resistant steel of the present invention that satisfies the above-described alloy composition preferably includes a martensite phase as a microstructure and a matrix structure.
보다 구체적으로, 본 발명의 내마모강은 면적분율 85% 이상(100% 포함)으로 마르텐사이트 상을 포함하며, 그 외 조직으로는 10% 이하의 베이나이트 상을 포함할 수 있으며, 잔여 조직은 페라이트이다. More specifically, the wear-resistant steel of the present invention contains a martensite phase at an area fraction of 85% or more (inclusive of 100%), and the other structure may include a bainite phase of 10% or less, and the remaining structure is It is ferrite.
상기 마르텐사이트 상의 분율이 85% 미만이면 목표 수준의 강도 및 경도의 확보가 어려워지는 문제가 있다.If the fraction of the martensite phase is less than 85%, there is a problem in that it becomes difficult to secure the target level of strength and hardness.
본 발명에 있어서, 상기 마르텐사이트 상은 템퍼드 마르텐사이트 상을 포함하며, 이와 같이 템퍼드 마르텐사이트 상을 포함하는 경우 강의 인성을 보다 유리하게 확보할 수 있다.In the present invention, the martensite phase includes a tempered martensite phase, and when the tempered martensite phase is included, the toughness of the steel can be more advantageously secured.
한편 본 발명은 강의 표면 경도를 480HB 이상, 중심 경도를 440HB 이상으로 확보할 수 있다. 여기서, 상기 '표면'은 강 표면부 예컨대 강 표면으로부터 두께 방향 2mm 직하의 영역을 지칭하며, 상기 '중심'은 강 두께 중심부 예컨대 1/2t, 1/4t(t는 강의 두께(mm)를 의미) 영역을 지칭할 수 있다. 다만, 이에 국한하는 것은 아니다.Meanwhile, the present invention can secure the surface hardness of the steel to 480 HB or more and the center hardness to 440 HB or more. Here, the 'surface' refers to the surface area of the steel, for example, an area directly under 2 mm in the thickness direction from the steel surface, and the 'center' refers to the center of the steel thickness, for example, 1/2t, 1/4t (t refers to the thickness of the steel (mm) ) can refer to an area. However, it is not limited to this.
다음으로, 본 발명의 다른 일 측면인, 고경도 내마모강을 제조하는 방법에 대하여 상세히 설명한다.Next, another aspect of the present invention, a method for manufacturing high hardness wear-resistant steel, will be described in detail.
간략히 설명하면, 앞서 서술한 합금조성을 만족하는 강 슬라브를 준비한 다음, 상기 강 슬라브를 [재가열 - 조압연 - 마무리 압연 - 공냉 - 재가열 열처리 - 냉각]하는 공정을 거쳐 제조하는 것이 바람직하다. 이하에서는 각 공정 조건에 대하여 상세히 설명한다.Briefly, it is preferable to prepare a steel slab that satisfies the alloy composition described above and then manufacture the steel slab through the following processes [reheating - rough rolling - finish rolling - air cooling - reheating heat treatment - cooling]. Below, each process condition is described in detail.
먼저, 본 발명에서 제안하는 합금조성을 만족하는 강 슬라브를 준비한 후, 이를 1050~1250℃의 온도범위에서 가열하는 것이 바람직하다.First, it is desirable to prepare a steel slab that satisfies the alloy composition proposed in the present invention and then heat it at a temperature range of 1050 to 1250°C.
상기 가열시 온도가 1050℃ 미만이면 Nb 등의 재고용이 충분하지 못하며, 반면 그 온도가 1250℃를 초과하게 되면 오스테나이트 결정립이 조대화되어 불균일한 조직이 형성될 우려가 있다.If the heating temperature is less than 1050°C, re-dissolution of Nb and the like is not sufficient. On the other hand, if the temperature exceeds 1250°C, there is a risk that austenite grains may become coarse and an uneven structure may be formed.
따라서, 본 발명에서는 강 슬라브의 가열시 1050~1250℃의 온도범위에서 실시하는 것이 바람직하다.Therefore, in the present invention, heating of the steel slab is preferably carried out in a temperature range of 1050 to 1250°C.
상기 가열된 강 슬라브를 조압연 및 마무리 압연을 거쳐 열연강판으로 제조하는 것이 바람직하다.It is preferable to manufacture the heated steel slab into a hot rolled steel sheet through rough rolling and finish rolling.
우선, 상기 가열된 강 슬라브를 950~1050℃의 온도범위에서 조압연하여 바(bar)로 제조한 후, 이것을 750~950℃의 온도범위에서 마무리 열간압연하는 것이 바람직하다.First, it is preferable to rough-roll the heated steel slab at a temperature range of 950 to 1050°C to produce a bar, and then perform final hot rolling at a temperature range of 750 to 950°C.
상기 조압연시 그 온도가 950℃ 미만이면 압연 하중이 증가하여 상대적으로 약압하 됨으로써 슬라브 두께 방향 중심까지 변형이 충분히 전달되지 못하여 공극과 같은 결함이 제거되지 않을 우려가 있다. 반면, 그 온도가 1050℃를 초과하게 되면 압연과 동시에 재결정이 일어난 후 입자가 성장하게 되어 초기 오스테나이트 입자가 지나치게 조대해질 우려가 있다.If the temperature during the rough rolling is less than 950°C, the rolling load increases and the pressure is relatively weak, so that the strain is not sufficiently transmitted to the center of the slab in the thickness direction, and there is a risk that defects such as voids may not be removed. On the other hand, if the temperature exceeds 1050°C, recrystallization occurs simultaneously with rolling and then grains grow, raising the risk that the initial austenite grains may become excessively coarse.
상기 마무리 온도범위가 750℃ 미만이면 2상역 압연이 되어 미세조직 중에 페라이트가 생성될 우려가 있으며, 반면 그 온도가 950℃를 초과하게 되면 압연롤 부하가 심해져 압연성이 열위하게 되는 문제가 있다.If the finishing temperature range is less than 750°C, there is a risk of ferrite being generated in the microstructure due to two-phase rolling. On the other hand, if the temperature exceeds 950°C, the rolling roll load increases and there is a problem of poor rolling performance.
상기한 바에 따라 제조된 열연강판을 상온까지 공냉한 후, 850~950℃의 온도범위에서 재로시간 20분 이상으로 재가열 열처리를 행하는 것이 바람직하다.After air cooling the hot rolled steel sheet manufactured as described above to room temperature, it is preferable to perform reheating heat treatment at a temperature range of 850 to 950°C for a reheating time of 20 minutes or more.
상기 재가열 열처리는 페라이트와 펄라이트로 구성된 열연강판을 오스테나이트 단상으로 역변태시키기 위한 것으로, 상기 재가열 열처리시 온도가 850℃ 미만이면 오스테나이트화가 충분히 이루어지지 못하여 조대한 연질 페라이트가 혼재하게 됨으로써 최종 제품의 경도가 저하되는 문제가 있다. 반면, 그 온도가 950℃를 초과하게 되면 오스테나이트 결정립이 조대해져 소입성이 커지는 효과는 있으나, 강의 저온인성이 열위해지는 문제가 있다.The reheat heat treatment is to reverse transform a hot rolled steel sheet composed of ferrite and pearlite into austenite single phase. If the temperature during the reheat heat treatment is less than 850°C, austenitization is not sufficiently achieved and coarse soft ferrite is mixed, thereby damaging the final product. There is a problem that hardness decreases. On the other hand, when the temperature exceeds 950°C, the austenite grains become coarse, which has the effect of increasing hardenability, but there is a problem in that the low-temperature toughness of the steel becomes inferior.
상술한 온도범위에서 재가열시 재로시간이 20분 미만이면 오스테나이트화가 충분히 일어나지 못하여 후속하는 급속냉각에 의한 상변태 즉, 마르텐사이트 조직을 충분히 얻을 수 없게 된다.If the re-heating time is less than 20 minutes when reheating in the above-mentioned temperature range, austenitization does not occur sufficiently, so phase transformation by subsequent rapid cooling, that is, martensite structure, cannot be sufficiently obtained.
상기 재가열 열처리를 완료한 후, 판 두께 중심부(예컨대 1/2t 지점 (여기서 t는 두께(mm)를 의미))를 기준으로 9.0℃/s 이상의 냉각속도로 200℃ 이하까지 냉각을 행하는 것이 바람직하다. 이때, 상기 냉각은 수냉인 것이 바람직하다.After completing the reheating heat treatment, it is preferable to cool to 200°C or less at a cooling rate of 9.0°C/s or more based on the center of the plate thickness (e.g., 1/2t point (where t means thickness (mm))). . At this time, the cooling is preferably water cooling.
상기 재가열 열처리 후 냉각시 냉각속도가 9.0℃/s 미만이거나 냉각종료온도가 200℃를 초과하게 되면 냉각 중 베이나이트 상 등이 과다하게 형성될 우려가 있다.If the cooling rate during cooling after the reheating heat treatment is less than 9.0°C/s or the cooling end temperature exceeds 200°C, there is a risk of excessive formation of a bainite phase during cooling.
본 발명에서 상기 냉각속도의 상한은 특별히 한정하지 아니하며, 설비 한계를 고려하여 적합하게 설정할 수 있다.In the present invention, the upper limit of the cooling rate is not particularly limited and can be set appropriately considering equipment limitations.
한편, 상기 재가열 열처리 및 냉각 공정을 완료한 열연강판은 바람직하게 40~80mm의 두께를 갖는 후강판이다. Meanwhile, the hot rolled steel sheet that has completed the reheating heat treatment and cooling processes is preferably a thick steel sheet with a thickness of 40 to 80 mm.
상술한 제조조건에 따라 제조된 본 발명의 열연강판은 미세조직으로 마르텐사이트 상을 주상으로 포함하며, 전 두께에 걸쳐 고경도를 가지는 효과가 있다.The hot-rolled steel sheet of the present invention manufactured according to the above-described manufacturing conditions contains martensite as the main phase in its microstructure, and has the effect of having high hardness throughout the entire thickness.
이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명하고자 한다. 다만, 하기의 실시예는 본 발명을 예시하여 보다 보다 상세하게 설명하기 위한 것일 뿐, 본 발명의 권리범위를 한정하기 위한 것이 아니라는 점에 유의할 필요가 있다. Hereinafter, the present invention will be described in more detail through examples. However, it should be noted that the following examples are only for illustrating the present invention and explaining it in more detail, and are not intended to limit the scope of the present invention.
(실시예)(Example)
중량%로, 탄소(C): 0.26%, 실리콘(Si): 0.26%, 망간(Mn): 1.2%, 인(P): 0.01%, 황(S): 0.001%, 알루미늄(Al): 0.03%, 크롬(Cr): 0.3%, 니켈(Ni): 0.04%, 몰리브덴(Mo): 0.01%, 보론(B): 0.0015%, 구리(Cu): 0.01%, 티타늄(Ti): 0.04%, 바나듐(V): 0.005%고, 잔부 Fe 및 기타 불가피한 불순물을 포함하는 슬라브를 마련하였다. 이어, 상기 슬라브를 1100℃에서 가열한 후 1000℃에서 조압연하였다. 그리고 상기 조압압된 슬라브는 850℃에서 마무리압연되어 두께 40mm의 열연강판을 제조한 후, 상온으로 공냉하였다. 후속하여, 상기 공냉된 열연강판을 900℃의 온도범위에서 재로시간 20분 이상으로 재가열 열처리한 후, 하기 표 1과 같이 냉각속도룰 달리하면서 200℃ 이하까지 냉각하였다. By weight percent: Carbon (C): 0.26%, Silicon (Si): 0.26%, Manganese (Mn): 1.2%, Phosphorus (P): 0.01%, Sulfur (S): 0.001%, Aluminum (Al): 0.03. %, chromium (Cr): 0.3%, nickel (Ni): 0.04%, molybdenum (Mo): 0.01%, boron (B): 0.0015%, copper (Cu): 0.01%, titanium (Ti): 0.04%, Vanadium (V): 0.005%, and a slab containing the balance Fe and other inevitable impurities was prepared. Next, the slab was heated at 1100°C and then rough-rolled at 1000°C. Then, the rough-pressed slab was finish rolled at 850°C to produce a hot-rolled steel sheet with a thickness of 40 mm, and then air-cooled to room temperature. Subsequently, the air-cooled hot-rolled steel sheet was reheated and heat-treated at a temperature range of 900°C for a reheat time of 20 minutes or more, and then cooled to 200°C or lower while varying the cooling rate as shown in Table 1 below.
이후, 각각의 열연강판에 대해 미세조직 및 기계적 물성을 측정하였다. 상기 미세조직은 임의의 크기로 시편을 절단하여 경면을 제작한 후 나이탈 에칭액을 이용하여 부식시킨 다음 광학현미경과 전자주사현미경을 활용하여 표층으로부터 두께 방향 2mm 위치와 두께 중심인 1/2t(mm) 위치를 모두 관찰하였으며, 그 관찰결과, 본 발명예 1-3의 경우, 면적분율 85% 이상의 마르텐사이트, 10% 이하의 베이나이트, 잔여 페라이트를 포함하는 미세조직을 가짐을 확인하였다. Afterwards, the microstructure and mechanical properties were measured for each hot rolled steel sheet. The microstructure was created by cutting a specimen to an arbitrary size to produce a mirror surface, then etching it using a nital etching solution, and then using an optical microscope and an electron scanning microscope to measure the thickness at a position of 2 mm from the surface layer and the center of the thickness at 1/2t (mm). ) All positions were observed, and as a result of the observation, it was confirmed that Inventive Examples 1-3 had a microstructure containing martensite with an area fraction of 85% or more, bainite with an area fraction of 10% or less, and residual ferrite.
한편 제조된 열연강판에 대한 비커스 경도를 측정하여 도 1에 나타내었다. 본 발명에서 비커스 경도는 비커스 경도시험기(하중 10kg, 대면각 136도 정사각형 다이아몬드 입자)를 이용하여 측정하였으며, 이때, 표면경도는 판 표면을 2mm 밀링가공 후 측정하였으며, 중심부 경도는 판 두께 방향으로 시편을 절단한 다음 두께의 중심 즉, 1/2t 위치에서 측정하였다.Meanwhile, the Vickers hardness of the manufactured hot rolled steel sheet was measured and shown in Figure 1. In the present invention, Vickers hardness was measured using a Vickers hardness tester (load 10 kg, square diamond particles with a face angle of 136 degrees). At this time, the surface hardness was measured after milling the plate surface by 2 mm, and the central hardness was measured by measuring the specimen in the direction of the plate thickness. was cut and measured at the center of the thickness, that is, at the 1/2t position.
또한 브리넬 경도는 브리넬 경도 시험기(하중 3000kgf, 10mm 텅스텐 압입 구)를 이용하여 측정하였으며, 이때, 표면 경도는 판 표면을 2mm 밀링 가공한 후 3회 측정한 것의 평균값을 사용하였으며, 단면 경도의 경우 판 두께 방향으로 시편을 절단한 다음 두께의 중심 즉, 1/2t 위치에서 3회 측정한 후 평균값을 사용하였다. In addition, Brinell hardness was measured using a Brinell hardness tester (load 3000kgf, 10mm tungsten indentation sphere). At this time, the surface hardness was the average value of three measurements after milling the plate surface 2mm, and for cross-sectional hardness, the plate The specimen was cut in the thickness direction, then measured three times at the center of the thickness, that is, at the 1/2t position, and the average value was used.
도 1은 본 발명의 일실시예 따른 냉각속도와 비커스 경도와의 상관관계를 보여주는 그림이다. Figure 1 is a diagram showing the correlation between cooling rate and Vickers hardness according to an embodiment of the present invention.
도 1에 나타난 바와 같이, 본 발명의 조건으로 재가열 후, 9.0℃/s 이상의 냉각속도로 열연강판을 냉각한 발명예 1-3의 경우가 비교예 17 대비 열연강판의 비커스 경도가 48Hv이상으로 우수함을 알 수 있다. As shown in Figure 1, in the case of Inventive Example 1-3, in which the hot-rolled steel sheet was cooled at a cooling rate of 9.0°C/s or more after reheating under the conditions of the present invention, the Vickers hardness of the hot-rolled steel sheet was superior to 48Hv or more compared to Comparative Example 17. can be seen.
한편 도 2 본 발명의 일실시예에 따른 재가열온도와 열연강판의 브리넬 경도와의 상관관계를 보여주는 그림으로서, 전술한 재가열한 온도가 850~950℃ 범위일때, 열연강판의 브리넬경도가 우수해짐을 알 수 있다. Meanwhile, Figure 2 is a diagram showing the correlation between the reheating temperature and the Brinell hardness of the hot-rolled steel sheet according to an embodiment of the present invention, showing that when the above-described reheating temperature is in the range of 850 to 950 ° C, the Brinell hardness of the hot-rolled steel sheet becomes excellent. Able to know.
도 3은 본 발명에 따른 개발재의 강판 두께에 따른 경도 프로파일을 종래재와 대비하여 나타낸 그림이다. 도 3에 나타난 바와 같이, 본 발명의 열연강판의 경우 종래재 대비 열연강판 두께에 따른 경도 편차가 적은 우수한 특성을 가짐을 알 수 있다. Figure 3 is a diagram showing the hardness profile according to the steel plate thickness of the developed material according to the present invention compared to the conventional material. As shown in Figure 3, it can be seen that the hot rolled steel sheet of the present invention has excellent properties with less hardness variation depending on the thickness of the hot rolled steel sheet compared to conventional materials.
이상에서 설명한 바와 같이, 본 발명의 상세한 설명에서는 본 발명의 바람직한 실시 예에 관하여 설명하였으나, 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자라면 본 발명의 범주에서 벗어나지 않는 한도 내에서 여러 가지 변형이 가능함은 물론이다. 따라서 본 발명의 권리 범위는 설명된 실시 예에 국한되어 정해져서는 안 되며, 후술하는 청구범위뿐만 아니라, 이와 균등한 것들에 의해 정해져야 한다.As described above, the detailed description of the present invention has described preferred embodiments of the present invention, but those skilled in the art can make various modifications without departing from the scope of the present invention. Of course this is possible. Therefore, the scope of rights of the present invention should not be limited to the described embodiments, but should be determined by the claims described below as well as their equivalents.
Claims (4)
In weight percent, carbon (C): 0.19~0.32%, silicon (Si): 0.1~0.7%, manganese (Mn): 0.6~1.6%, phosphorus (P): 0.05% or less (excluding 0), sulfur ( S): 0.02% or less (excluding 0), Aluminum (Al): 0.07% or less (excluding 0), Chromium (Cr): 0.1 to 1.5%, Nickel (Ni): 0.01 to 2.0%, Molybdenum (Mo) : 0.01~0.8%, Boron (B): 50ppm or less (excluding 0), Cobalt (Co): Contains 0.04% or less, Copper (Cu): 0.5% or less (excluding 0), Titanium (Ti): 0.04 % or less (excluding 0), Niobium (Nb): 0.05% or less (excluding 0), Vanadium (V): 0.05% or less (excluding 0), and Calcium (Ca): one or more of 2 to 100 ppm. A high-hardness wear-resistant steel whose microstructure contains martensite with an area fraction of 85% or more, bainite with an area fraction of 10% or less, and residual ferrite, including the balance of Fe and other inevitable impurities.
The method of claim 1, wherein arsenic (As): 0.05% or less (excluding 0), tin (Sn): 0.05% or less (excluding 0), and tungsten (W): 0.05% or less (excluding 0). more High hardness wear-resistant steel further comprising:
상기 강 슬라브를 1050~1250℃의 온도범위에서 가열하는 단계;
상기 재가열된 강 슬라브를 950~1050℃의 온도범위에서 조압연하는 단계; 상기 조압연 후 750~950℃의 온도범위에서 마무리 압연하여 열연강판을 제조하는 단계;
상기 열연강판을 상온까지 공냉 후, 850~950℃의 온도범위에서 재로시간 20분 이상으로 재가열 열처리하는 단계; 및
상기 재가열 열처리 후 상기 열연강판을 9.0℃/s 이상의 냉각속도로 200℃ 이하까지 냉각하는 단계를 포함하는 고경도 내마모강의 제조방법.
In weight percent, carbon (C): 0.19~0.32%, silicon (Si): 0.1~0.7%, manganese (Mn): 0.6~1.6%, phosphorus (P): 0.05% or less (excluding 0), sulfur ( S): 0.02% or less (excluding 0), Aluminum (Al): 0.07% or less (excluding 0), Chromium (Cr): 0.1 to 1.5%, Nickel (Ni): 0.01 to 2.0%, Molybdenum (Mo) : 0.01~0.8%, Boron (B): 50ppm or less (excluding 0), Cobalt (Co): Contains 0.04% or less, Copper (Cu): 0.5% or less (excluding 0), Titanium (Ti): 0.04 % or less (excluding 0), Niobium (Nb): 0.05% or less (excluding 0), Vanadium (V): 0.05% or less (excluding 0), and Calcium (Ca): one or more of 2 to 100 ppm. preparing a steel slab containing the balance Fe and other unavoidable impurities;
Heating the steel slab at a temperature range of 1050 to 1250°C;
Rough rolling the reheated steel slab at a temperature range of 950 to 1050°C; Manufacturing a hot-rolled steel sheet by performing finish rolling at a temperature range of 750 to 950° C. after the rough rolling;
Air-cooling the hot-rolled steel sheet to room temperature and then reheating and heat-treating the hot-rolled steel sheet at a temperature range of 850 to 950°C for a reheat time of 20 minutes or more; and
A method of manufacturing high hardness wear-resistant steel comprising the step of cooling the hot rolled steel sheet to 200°C or less at a cooling rate of 9.0°C/s or more after the reheating heat treatment.
The method of claim 3, wherein one of arsenic (As): 0.05% or less (excluding 0), tin (Sn): 0.05% or less (excluding 0), and tungsten (W): 0.05% or less (excluding 0). more A method for manufacturing high hardness wear-resistant steel and wear-resistant steel further comprising:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020220179266A KR20240098230A (en) | 2022-12-20 | 2022-12-20 | Wear resistant steel havinh high hardness and method for manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020220179266A KR20240098230A (en) | 2022-12-20 | 2022-12-20 | Wear resistant steel havinh high hardness and method for manufacturing the same |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| KR20240098230A true KR20240098230A (en) | 2024-06-28 |
Family
ID=91669244
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020220179266A KR20240098230A (en) | 2022-12-20 | 2022-12-20 | Wear resistant steel havinh high hardness and method for manufacturing the same |
Country Status (1)
| Country | Link |
|---|---|
| KR (1) | KR20240098230A (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0841535A (en) | 1994-07-29 | 1996-02-13 | Nippon Steel Corp | Production of high hardness wear resistant steel excellent in low temperature toughness |
-
2022
- 2022-12-20 KR KR1020220179266A patent/KR20240098230A/en unknown
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0841535A (en) | 1994-07-29 | 1996-02-13 | Nippon Steel Corp | Production of high hardness wear resistant steel excellent in low temperature toughness |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110100034B (en) | High-hardness wear-resistant steel and method for manufacturing same | |
| KR102119959B1 (en) | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same | |
| JP7018510B2 (en) | Wear-resistant steel with excellent hardness and impact toughness and its manufacturing method | |
| KR102175570B1 (en) | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same | |
| KR102314432B1 (en) | Wear resistant steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR101899687B1 (en) | Wear resistant steel having high hardness and method for manufacturing same | |
| KR101736621B1 (en) | High hardness anti-abrasion steel having excellent toughness and superior resistance to cracking during thermal cutting | |
| JP7018509B2 (en) | Wear-resistant steel with excellent hardness and impact toughness and its manufacturing method | |
| KR20240098230A (en) | Wear resistant steel havinh high hardness and method for manufacturing the same | |
| KR101675677B1 (en) | Non-heated hot-rolled steel sheet and method of manufacturing the same | |
| KR102560057B1 (en) | High yield ratio and high strength steel sheet having excellent bendability and the method for manufacturing the same | |
| KR102239184B1 (en) | Steel plate having excellent strength and low-temperature impact toughness and method for manufacturing thereof | |
| KR102498150B1 (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR102498144B1 (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR102348555B1 (en) | Abrasion resistant steel with excellent cutting crack resistance and method of manufacturing the same | |
| KR20220088242A (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR20220089109A (en) | High-strength steel plate for pressure vessels with excellent impact toughness and manufacturing method thereof | |
| KR20220088233A (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR20220088240A (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
| KR20220088239A (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof |