CA3113056C - Abrasion resistant steel having excellent hardness and impact toughness and manufacturing method therefor - Google Patents
Abrasion resistant steel having excellent hardness and impact toughness and manufacturing method therefor Download PDFInfo
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- CA3113056C CA3113056C CA3113056A CA3113056A CA3113056C CA 3113056 C CA3113056 C CA 3113056C CA 3113056 A CA3113056 A CA 3113056A CA 3113056 A CA3113056 A CA 3113056A CA 3113056 C CA3113056 C CA 3113056C
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 114
- 239000010959 steel Substances 0.000 title claims abstract description 114
- 238000005299 abrasion Methods 0.000 title claims abstract description 40
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 28
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 54
- 239000011575 calcium Substances 0.000 claims abstract description 28
- 239000010955 niobium Substances 0.000 claims abstract description 28
- 239000010936 titanium Substances 0.000 claims abstract description 25
- 239000011651 chromium Substances 0.000 claims abstract description 23
- 239000010949 copper Substances 0.000 claims abstract description 23
- 239000011572 manganese Substances 0.000 claims abstract description 21
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 18
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 17
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 13
- 239000012535 impurity Substances 0.000 claims abstract description 11
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 10
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 10
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 10
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 9
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 9
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 9
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 9
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 9
- 229910052796 boron Inorganic materials 0.000 claims abstract description 9
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 239000010941 cobalt Substances 0.000 claims abstract description 9
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 9
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 239000011733 molybdenum Substances 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 239000011574 phosphorus Substances 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 239000010703 silicon Substances 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 239000011593 sulfur Substances 0.000 claims abstract description 9
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims description 27
- 238000003303 reheating Methods 0.000 claims description 18
- 238000005096 rolling process Methods 0.000 claims description 14
- 229910052718 tin Inorganic materials 0.000 claims description 11
- 229910052721 tungsten Inorganic materials 0.000 claims description 10
- 229910052785 arsenic Inorganic materials 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000010521 absorption reaction Methods 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 8
- 238000000034 method Methods 0.000 claims description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 7
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 6
- 239000010937 tungsten Substances 0.000 claims description 6
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims description 5
- 230000000052 comparative effect Effects 0.000 description 19
- 229910045601 alloy Inorganic materials 0.000 description 14
- 239000000956 alloy Substances 0.000 description 14
- 230000000694 effects Effects 0.000 description 14
- 239000000203 mixture Substances 0.000 description 12
- 229910001566 austenite Inorganic materials 0.000 description 11
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 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
- 230000002596 correlated effect Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000005065 mining Methods 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
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- 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
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- 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
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- 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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
One embodiment of the present invention provides an abrasion resistant steel having excellent hardness and impact toughness, and a manufacturing method therefor, the abrasion resistant steel comprising, by wt%, 0.33-0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.07% or less of aluminum (Al) (excluding 0), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8% of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 50 ppm or less of boron (B) (excluding 0), and 0.02% or less of cobalt (Co) (excluding 0), further comprising one or more selected from the group consisting of 0.02% or less of titanium (Ti) (excluding 0), 0.05% or less of niobium (Nb) (excluding 0), 0.05% or less of vanadium (V) (excluding 0) and 2-100 ppm of calcium (Ca), and comprising the balance of Fe and other inevitable impurities, wherein C and Ni satisfy the following relation 1, and the microstructure comprises 95 area% or more of martensite and 5% or less of bainite (including 0%). [Relation 1] [C]×[Ni] = 0.231
Description
CA 031.13056 2021-03-16 [DESCRIPTION]
[Invention Title]
ABRASION RESISTANT STEEL HAVING EXCELLENT HARDNESS AND
IMPACT TOUGHNESS AND MANUFACTURING METHOD THEREFOR
[Technical Field]
[0001] The present disclosure relates to a high hardness abrasion resistant steel and a manufacturing method therefor, and more particularly, to a high hardness abrasion resistant steel which may be used for construction machinery, and the like, and a manufacturing method therefor.
[Background Art]
[Invention Title]
ABRASION RESISTANT STEEL HAVING EXCELLENT HARDNESS AND
IMPACT TOUGHNESS AND MANUFACTURING METHOD THEREFOR
[Technical Field]
[0001] The present disclosure relates to a high hardness abrasion resistant steel and a manufacturing method therefor, and more particularly, to a high hardness abrasion resistant steel which may be used for construction machinery, and the like, and a manufacturing method therefor.
[Background Art]
[0002] As for construction machinery and industrial machinery used in many industrial fields such as construction, civil engineering, mining, and cement industries, since abrasion may occur severely due to friction in operation, it may be necessary to apply a material exhibiting abrasion resistance properties.
[0003] Generally, as abrasion resistance and hardness of a thick steel sheet maybe correlated with each other, it maybe necessary to increase hardness in the thick steel sheet concerned, to be worn down. To secure stable abrasion resistance, it may be necessary to have uniform hardness from the surface of the thick steel sheet to the inside (around t/2, t = thickness) of the sheet thickness (that is, having the same degree of Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 hardness on the surface of the thick steel sheet and inside).
[0004] Generally, to obtain high hardness in a thick steel sheet, a method of reheating to an Ac3 temperature or higher after rolling and quenching may be widely used. For example, cited references 1 and 2 disclose a method of increasing a content of C and adding a large amount of hardenability enhancing elements such as Cr and Mo, thereby increasing surface hardness. However, to manufacture an extremely thick steel sheet, it may be necessary to add a greater amount of hardenability elements to secure hardenability in the center of the steel sheet, and as C and hardenability alloys are added in large amounts, manufacturing costs may increase, and weldability and low-temperature toughness may degrade, which may be problematic.
[0005] Therefore, while it is inevitable to add hardenability alloys to secure hardenability, it has been necessary to devise a measure for obtaining excellent abrasion resistance by securing high hardness, and securing high strength and high impact toughness.
[Reference]
(Reference 1) Japanese Laid-Open Patent Publication No.
(Reference 2) Japanese Laid-Open Patent Publication No.
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 [Disclosure]
[Technical Problem]
[Reference]
(Reference 1) Japanese Laid-Open Patent Publication No.
(Reference 2) Japanese Laid-Open Patent Publication No.
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 [Disclosure]
[Technical Problem]
[0006] An aspect of the present disclosure may be to provide a high hardness abrasion resistant steel which may have excellent abrasion resistance and also high strength and high impact toughness, and a manufacturing method therefor.
[Technical Solution]
[Technical Solution]
[0007] An example embodiment of the present disclosure provides an abrasion resistant steel having excellent hardness and impact toughness including, by weight%, 0.33-0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0 . 6-1 . 6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.07% or less of aluminum (Al) (excluding 0), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0. 01-0 . 8% of chromium (Cr), 0 . 01-0 . 8% of molybdenum (Mo), 50 ppm or less of boron (B) (excluding 0), and 0.02% or less of cobalt (Co) (excluding 0) and further comprising one or more selected from a group consisting of 0.02% or less of titanium (Ti) (excluding 0), 0.05% or less of niobium (Nb) (excluding 0), 0.05% or less of vanadium (V) (excluding 0) and 2-100 ppm of calcium (Ca), with a balance of Fe and other inevitable impurities, wherein C and Ni satisfy relational expression 1 as below, and wherein a microstructure includes 95 area% or more Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 of martensite and 5% or less of bainite (including 0%).
[Relational Expression 1] [C]x[Ni] 0.231
[Relational Expression 1] [C]x[Ni] 0.231
[0008] Another example embodiment of the present disclosure provides a method of manufacturing an abrasion resistant steel having excellent hardness and impact toughness including heating a steel slab including, byweight%, 0 .33-0 .42% of carbon (C), 0.1-0.7% of silicon (Si), 0 . 6-1. 6% ofmanganese (Mn), 0.05%
or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (8) (excluding 0), 0.07% or less of aluminum (Al) (excluding 0), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8% of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 50 ppm or less of boron (B) (excluding 0), and 0.02% or less of cobalt (Co) (excluding 0) and further comprising one or more selected from a group consisting of 0.02% or less of titanium (Ti) (excluding 0), 0.05% or less of niobium (Nb) (excluding 0), 0.05% or less of vanadium (V) (excluding 0) and 2-100 ppm of calcium (Ca), with a balance of Fe and other inevitable impurities, where C and Ni satisfy relational expression 1 as below, in a temperature range of 1050-1250 C; obtaining a rough-rolled bar by rough-rolling the reheated steel slab in a temperature range of 950-1050 C; obtaining a hot-rolled steel sheet by finishing-hot-rolling the rough-rolled bar in a temperature range of 850-950 C; air-cooling the hot-rolled steel sheet to room temperature and reheating the steel sheet for a residence time of 1.3t+10min-1.3t+60min (t: sheet Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 thickness) in a temperature range of 860-950 C; and water-cooling the reheated hot-rolled steel sheet to 150 C or less.
[Relational Expression 1] [C] x [Ni] 0.231 [Advantageous Effects]
or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (8) (excluding 0), 0.07% or less of aluminum (Al) (excluding 0), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8% of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 50 ppm or less of boron (B) (excluding 0), and 0.02% or less of cobalt (Co) (excluding 0) and further comprising one or more selected from a group consisting of 0.02% or less of titanium (Ti) (excluding 0), 0.05% or less of niobium (Nb) (excluding 0), 0.05% or less of vanadium (V) (excluding 0) and 2-100 ppm of calcium (Ca), with a balance of Fe and other inevitable impurities, where C and Ni satisfy relational expression 1 as below, in a temperature range of 1050-1250 C; obtaining a rough-rolled bar by rough-rolling the reheated steel slab in a temperature range of 950-1050 C; obtaining a hot-rolled steel sheet by finishing-hot-rolling the rough-rolled bar in a temperature range of 850-950 C; air-cooling the hot-rolled steel sheet to room temperature and reheating the steel sheet for a residence time of 1.3t+10min-1.3t+60min (t: sheet Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 thickness) in a temperature range of 860-950 C; and water-cooling the reheated hot-rolled steel sheet to 150 C or less.
[Relational Expression 1] [C] x [Ni] 0.231 [Advantageous Effects]
[0009] According to an aspect of the present disclosure, an effect of providing an abrasion resistant steel having a thickness of 60mm or less and having high hardness and excellent low-temperature toughness may be obtained.
[Best Mode for Invention]
[Best Mode for Invention]
[0010] In the description below, the present disclosure will be described in detail. The alloy composition of the present disclosure will be described first. The content of the alloy composition described below may be represented by weight%.
Carbon (C): 0.33-0.42%
Carbon (C): 0.33-0.42%
[0011] Carbon (C) may be effective in increasing strength and hardness in a steel having a martensite structure and may be effective for improving hardenability. To sufficiently secure the above-described effect, it may be preferable to add C by 0.33% or more. However, when the content thereof exceeds 0.42%, weldability and toughness may degrade, such that an additional heat treatment such as tempering may be inevitable. Therefore, in the present disclosure, it may be preferable to control the Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 content of C to be 0.33-0.42%. A lower limit of the content of C may more preferably be 0.34%, even more preferably 0.35%, and most preferably 0.36%. An upper limit of the content of C may more preferably be 0.40%, even more preferably 0.39%, and most preferably 0.38%.
Silicon (Si) : 0.1-0.7%
Silicon (Si) : 0.1-0.7%
[0012] Silicon (Si) may be effective in improving strength according to deoxidation and solid solution strengthening. To obtain the above effect, it may be preferable to add Si by 0.1%
or more. However, when the content thereof exceeds 0.7%, weldability may deteriorate, which may not be preferable.
Therefore, in the present disclosure, it may be preferable to control the content of Si to be 0.1-0.7%. A lower limit of the content of Si may more preferably be 0.12%, even more preferably 0.15%, and most preferably 0.2%. An upper limit of the Si content may more preferably be 0.5%, even more preferably 0.45%, and most preferably 0.4%.
Manganese (Mn) : 0.6-1.6%
or more. However, when the content thereof exceeds 0.7%, weldability may deteriorate, which may not be preferable.
Therefore, in the present disclosure, it may be preferable to control the content of Si to be 0.1-0.7%. A lower limit of the content of Si may more preferably be 0.12%, even more preferably 0.15%, and most preferably 0.2%. An upper limit of the Si content may more preferably be 0.5%, even more preferably 0.45%, and most preferably 0.4%.
Manganese (Mn) : 0.6-1.6%
[0013] Manganese (Mn) may suppress ferrite formation and may effectively improve hardenability by decreasing Ar3 temperature, thereby improving strength and toughness of steel.
In the present disclosure, to secure hardness of the thick steel material, it may be preferable to include Mn in an amount of 0.6% or more. When the content exceeds 1.6%, weldability may degrade. Therefore, in the present disclosure, it may be Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 preferable to control the content of Mn to be 0.6-1.6%. A lower limit of the content of Mn may more preferably be 0.65%, even more preferably 0 . 70%, and most preferably 0 . 75% . An upper limit of the content of Mn may more preferably be 1.55%, even more preferably 1.50%, and most preferably 1.45%.
Phosphorus (P): 0.05% or less (excluding 0)
In the present disclosure, to secure hardness of the thick steel material, it may be preferable to include Mn in an amount of 0.6% or more. When the content exceeds 1.6%, weldability may degrade. Therefore, in the present disclosure, it may be Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 preferable to control the content of Mn to be 0.6-1.6%. A lower limit of the content of Mn may more preferably be 0.65%, even more preferably 0 . 70%, and most preferably 0 . 75% . An upper limit of the content of Mn may more preferably be 1.55%, even more preferably 1.50%, and most preferably 1.45%.
Phosphorus (P): 0.05% or less (excluding 0)
[0014] Phosphorus (P) maybe inevitably included in steel, and may degrade toughness of steel. Therefore, it may be preferable to control the content of P to be less than 0.05% by lowering the content as much as possible, but 0% may be excluded in consideration of the inevitably included amount. The content of P may more preferably be 0.03% or less, even more preferably 0.02% or less, and most preferably 0.01% or less.
Sulfur (S): 0.02% or less (excluding 0)
Sulfur (S): 0.02% or less (excluding 0)
[0015] Sulfur (S) may deteriorate toughness of steel by forming an MnS inclusion in steel. Therefore, it may be preferable to control the content of S to be 0.02% or less by lowering the content as much as possible, but 0% may be excluded in consideration of the inevitably included amount. The content of S may more preferably be 0.01% or less, even more preferably 0.005% or less, and most preferably 0.003% or less.
Aluminum (Al): 0.07% or less (excluding 0)
Aluminum (Al): 0.07% or less (excluding 0)
[0016] Aluminum (Al) may be effective in lowering an oxygen content in molten steel as a deoxidizing agent for steel. When the content of Al exceeds 0.07%, cleanliness of the steel may Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 be impaired, which may not be preferable. Therefore, in the present disclosure, it may be preferable to control the content of Al to be 0.07% or less, and 0% may be excluded in consideration of load and an increase in manufacturing costs in the steelmaking process. The content of Al may more preferably be 0.05% or less, even more preferably 0.04% or less, and most preferably 0.03% or less.
Nickel (Ni): 0.55-5.0%
Nickel (Ni): 0.55-5.0%
[0017] Nickel (Ni) may be generally effective in improving toughness along with strength of steel. To obtain the above-described effect, it may be preferable to add Ni in an amount of 0.55% or more. However, when the content thereof exceeds 5.0%, the manufacturing costs may increase as Ni is an expensive element. Therefore, in the present disclosure, it may be preferable to control the content of Ni to be 0.55-5.0%. A
lower limit of the content of Ni may more preferably be 0.6%, even more preferably 0.7%, and most preferably 0.8%. An upper limit of the content of Ni may more preferably be 4.5%, even more preferably 4.0%, and most preferably 3.5%.
Copper (Cu): 0.01-1.5%
lower limit of the content of Ni may more preferably be 0.6%, even more preferably 0.7%, and most preferably 0.8%. An upper limit of the content of Ni may more preferably be 4.5%, even more preferably 4.0%, and most preferably 3.5%.
Copper (Cu): 0.01-1.5%
[0018] Copper (Cu) may simultaneously increase strength and toughness of steel along with Ni. To obtain the above effect, it may be preferable to add Cu in an amount of 0.01% or more.
However, when the content of Cu exceeds 1.5%, possibility of surface defects may increase, and hot workability may be Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 deteriorated. Therefore, in the present disclosure, it maybe preferable to control the content of Cu to be 0.01-1.5%. A lower limit of the content of Cu may more preferably be 0.05%, even more preferably 0 . 10%, andmost preferably 0 . 15% . An upper limit of the Cu content may more preferably be 1.2%, even more preferably 1.0%, and most preferably 0.8%.
Chrome (Cr): 0.01-0.8%
However, when the content of Cu exceeds 1.5%, possibility of surface defects may increase, and hot workability may be Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 deteriorated. Therefore, in the present disclosure, it maybe preferable to control the content of Cu to be 0.01-1.5%. A lower limit of the content of Cu may more preferably be 0.05%, even more preferably 0 . 10%, andmost preferably 0 . 15% . An upper limit of the Cu content may more preferably be 1.2%, even more preferably 1.0%, and most preferably 0.8%.
Chrome (Cr): 0.01-0.8%
[0019] Chromium (Cr) may increase strength of steel by increasing hardenability, and may be advantageous in securing hardness. To obtain the above-described effect, it may be preferable to add Cr in an amount of 0.01% or more, but when the content thereof exceeds 0.8%, weldability may be deteriorated and the manufacturing costs may increase.
Therefore, in the present disclosure, it may be preferable to control the content of Cr to be 0.01-0.8%. A lower limit of the Cr content may more preferably be 0.1%, even more preferably 0.15%, and most preferably 0.2%. An upper limit of the content of Cr may more preferably be 0.75%, even more preferably 0.70%, and most preferably 0.65%.
Molybdenum (Mo): 0.01-0.8%
Therefore, in the present disclosure, it may be preferable to control the content of Cr to be 0.01-0.8%. A lower limit of the Cr content may more preferably be 0.1%, even more preferably 0.15%, and most preferably 0.2%. An upper limit of the content of Cr may more preferably be 0.75%, even more preferably 0.70%, and most preferably 0.65%.
Molybdenum (Mo): 0.01-0.8%
[0020] Molybdenum (Mo) may increase hardenability of steel, and may be effective in improving hardness of a thick steel material. To sufficiently obtain the above-described effect, it may be preferable to add Mo in an amount of 0.01% or more.
However, as Mo is also an expensive element, when the content Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 thereof exceeds 0.8%, the manufacturing costs may increase, and weldability may degrade. Therefore, in the present disclosure, it may be preferable to control the content of Mo to be 0.01-0.8%.
A lower limit of the content of Mo may more preferably be 0.1%, even more preferably 0.12%, and most preferably 0.15%. An upper limit of the Mo content may more preferably be 0.75%, even more preferably 0.72%, and most preferably 0.70%.
Boron (B) : 50ppm or less (excluding 0)
However, as Mo is also an expensive element, when the content Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 thereof exceeds 0.8%, the manufacturing costs may increase, and weldability may degrade. Therefore, in the present disclosure, it may be preferable to control the content of Mo to be 0.01-0.8%.
A lower limit of the content of Mo may more preferably be 0.1%, even more preferably 0.12%, and most preferably 0.15%. An upper limit of the Mo content may more preferably be 0.75%, even more preferably 0.72%, and most preferably 0.70%.
Boron (B) : 50ppm or less (excluding 0)
[0021] Boron (B) may be effective in improving strength by effectively increasing hardenability of steel even by adding a small amount of B. When the content thereof is excessive, however, toughness and weldability of steel may be deteriorated, and thus, it may be preferable to control the content to be 50 ppm or less. A lower limit of the content of B may more preferably be 2 ppm, even more preferably 3 ppm, and most preferably 5 ppm.
An upper limit of the content of B may more preferably be 40 ppm, even more preferably 35 ppm, and most preferably 30 ppm.
Cobalt (Co) : 0.02% or less (excluding 0)
An upper limit of the content of B may more preferably be 40 ppm, even more preferably 35 ppm, and most preferably 30 ppm.
Cobalt (Co) : 0.02% or less (excluding 0)
[0022] Cobalt (Co) may be advantageous in securing hardness as well as strength of steel by increasing hardenability of steel. When the content thereof exceeds 0.02%, hardenability of the steel may decrease, and may increase the manufacturing costs as Co is an expensive element. Therefore, in the present disclosure, it may be preferable to add Co by 0.02% or less.
A lower limit of the Co content may more preferably be 0.001%, Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 even more preferably 0.002% or less, and most preferably 0.003%
or less. An upper limit of the Co content may more preferably be 0.018%, even more preferably 0.015%, and most preferably 0.013%.
A lower limit of the Co content may more preferably be 0.001%, Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 even more preferably 0.002% or less, and most preferably 0.003%
or less. An upper limit of the Co content may more preferably be 0.018%, even more preferably 0.015%, and most preferably 0.013%.
[0023] In addition to the above-described alloy composition, the abrasion-resistant steel in the present disclosure may further include elements advantageous for securing physical properties aimed in the present disclosure. For example, the abrasion-resistant steel may further include one or more selected from a group consisting of 0.02% or less of titanium (Ti) (excluding 0), 0.05% or less of niobium (Nb) (excluding 0), 0.05% or less of vanadium (V) (excluding 0) and 2-100 ppm of calcium (Ca).
Titanium (Ti): 0.02% or less (excluding 0)
Titanium (Ti): 0.02% or less (excluding 0)
[0024] Titanium (Ti) may maximize the effect of B, an element effective in improving hardenability of steel. Specifically, Ti may form a TIN precipitate by being combined with nitrogen (N), such that formation of BN may be prevented. Accordingly, solid solute B may increase, such that improvement of hardenability may be maximized. When the content of Ti exceeds 0.02%, a coarse TiN precipitate may be formed, such that toughness of the steel may deteriorate. Therefore, in the present disclosure, it may be preferable to add Ti by 0.02% or less. A lower limit of the content of Ti may more preferably be 0.005%, even more preferably 0.007%, and most preferably Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 0.010%. An upper limit of the content of Ti may more preferably be 0.019%, even more preferably 0.017%, and most preferably 0.015%.
Niobium (Nb): 0.05% or less (excluding 0)
Niobium (Nb): 0.05% or less (excluding 0)
[0025] Niobium (Nb) may be solid-solute in austenite and may increase hardenability of austenite, and may form carbonitride such as Nb (C,N) such that Nb may be effective for increasing strength of steel and inhibiting austenite grain growth. When the content of Nb exceeds 0.05%, a coarse precipitate may be formed, which becomes a starting point of brittle fracture, such that toughness may degrade. Therefore, in the present disclosure, it may be preferable to add Nb by 0.05% or less.
A lower limit of the content of Nb may more preferably be 0.002%, even more preferably 0.003%, and most preferably 0.005%. An upper limit of the content of Nb may more preferably be 0.040%, even more preferably 0.035%, and most preferably 0.030%.
Vanadium (V): 0.05% or less (excluding 0)
A lower limit of the content of Nb may more preferably be 0.002%, even more preferably 0.003%, and most preferably 0.005%. An upper limit of the content of Nb may more preferably be 0.040%, even more preferably 0.035%, and most preferably 0.030%.
Vanadium (V): 0.05% or less (excluding 0)
[0026] Vanadium (V) may form a VC carbide during reheating after hot-rolling, such that growth of austenite grains maybe inhibited, and V may be advantageous to securing strength and toughness by improving hardenability of steel. As V is an expensive element, when the content thereof exceeds 0.05%, V
may become a factor increasing the manufacturing costs.
Therefore, in the present disclosure, it may be preferable to control the content thereof to be 0.05% or less. A lower limit Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 of the content of V may more preferably be 0.002%, even more preferably 0.003%, and most preferably 0.005%. An upper limit of the content of V may more preferably be 0.045%, even more preferably 0.042%, and most preferably 0.040%.
Calcium (Ca) : 2-100ppm
may become a factor increasing the manufacturing costs.
Therefore, in the present disclosure, it may be preferable to control the content thereof to be 0.05% or less. A lower limit Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 of the content of V may more preferably be 0.002%, even more preferably 0.003%, and most preferably 0.005%. An upper limit of the content of V may more preferably be 0.045%, even more preferably 0.042%, and most preferably 0.040%.
Calcium (Ca) : 2-100ppm
[0027] Calcium (Ca) may have good bonding strength with S such that Ca may have an effect of inhibiting formation of MnS
segregated in a center of a thickness of a steel material by generating CaS. Also, CaS created by adding Ca may have an effect of increasing corrosion resistance in a humid external environment. To obtain the above-described effect, it may be preferable to add Ca in an amount of 2 ppm or more. However, when the content thereof exceeds 100 ppm, it may not be preferable as Ca may cause clogging of a nozzle in steelmaking.
Therefore, in the present disclosure, it may be preferable to control the content of Ca to be 2-100 ppm. A lower limit of the content of Ca may more preferably be 3 ppm, even more preferably 4 ppm, and most preferably 5 ppm. An upper limit of the content of Ca may more preferably be 80 ppm, even more preferably 60 ppm, and most preferably 40 ppm.
segregated in a center of a thickness of a steel material by generating CaS. Also, CaS created by adding Ca may have an effect of increasing corrosion resistance in a humid external environment. To obtain the above-described effect, it may be preferable to add Ca in an amount of 2 ppm or more. However, when the content thereof exceeds 100 ppm, it may not be preferable as Ca may cause clogging of a nozzle in steelmaking.
Therefore, in the present disclosure, it may be preferable to control the content of Ca to be 2-100 ppm. A lower limit of the content of Ca may more preferably be 3 ppm, even more preferably 4 ppm, and most preferably 5 ppm. An upper limit of the content of Ca may more preferably be 80 ppm, even more preferably 60 ppm, and most preferably 40 ppm.
[0028] Also, the abrasion resistant steel in the present disclosure may further include one or more selected from a group consisting of 0.05% or less of arsenic (As) (excluding 0) , 0.05%
or less of tin (Sn) (excluding 0) , and 0.05% or less of tungsten (W) (excluding 0) .
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16
or less of tin (Sn) (excluding 0) , and 0.05% or less of tungsten (W) (excluding 0) .
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16
[0029] As may be effective in improving toughness of steel, and Sn may be effective in improving strength and corrosion resistance of steel. Also, W may increase hardenability such that W may be effective in improving strength and also improving hardness at high temperature. When each content of As, Sn, and W exceeds 0.05%, the manufacturing costs may increase, and physical properties of steel may rather be deteriorated.
Therefore, in the present disclosure, when As, Sn and W are additionally included, it may be preferable to control each content thereof to be 0.05% or less . A lower limit of each content of As, Sn, and W may more preferably be 0.001%, even more preferably 0.002%, and most preferably 0.003%. An upper limit of each content of As, Sn and W may more preferably be 0.04%, even more preferably 0.03%, and most preferably 0.02%.
Therefore, in the present disclosure, when As, Sn and W are additionally included, it may be preferable to control each content thereof to be 0.05% or less . A lower limit of each content of As, Sn, and W may more preferably be 0.001%, even more preferably 0.002%, and most preferably 0.003%. An upper limit of each content of As, Sn and W may more preferably be 0.04%, even more preferably 0.03%, and most preferably 0.02%.
[0030] A remainder of the present disclosure may be iron (Fe) .
However, in a general manufacturing process, inevitable impurities may be inevitably added from raw materials or an ambient environment, and thus, impurities may not be excluded.
A person skilled in the art of a general manufacturing process may be aware of the impurities, and thus, the descriptions of the impurities may not be provided in the present disclosure.
However, in a general manufacturing process, inevitable impurities may be inevitably added from raw materials or an ambient environment, and thus, impurities may not be excluded.
A person skilled in the art of a general manufacturing process may be aware of the impurities, and thus, the descriptions of the impurities may not be provided in the present disclosure.
[0031] In the abrasion resistant steel in the present disclosure, it may be preferable for C and Ni of the above-described alloy composition to satisfy relational expression 1 as below. In the present disclosure, ultra-high Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 hardness and also excellent low-temperature toughness may be secured, and to this end, relational expression 1 should be satisfied preferably. When relational expression 1 is not satisfied, it may be difficult to improve both hardness and low temperature toughness to an excellent level. Therefore, a value of [C] x [Ni] may preferably be 0 .231 or more. A value of [C] x [Ni]
may more preferably be 0.396 or more, even more preferably 0.792 or more, and most preferably 1 or more. The higher the value of [C] [Ni] , the more advantageous the effect may be implemented, and thus, an upper limit of the value of [C] x [Ni] may not be particularly limited in the present disclosure.
may more preferably be 0.396 or more, even more preferably 0.792 or more, and most preferably 1 or more. The higher the value of [C] [Ni] , the more advantageous the effect may be implemented, and thus, an upper limit of the value of [C] x [Ni] may not be particularly limited in the present disclosure.
[0032] [Relational Expression 1] [C] x [Ni] 0.231
[0033] It may be preferable for a microstructure of the abrasion resistant steel in the present disclosure to include martensite as a matrix structure. More specifically, the abrasion resistant steel in the present disclosure may include 95% or more (including 100%) of martensite by an area fraction.
When the fraction of martensite is less than 95%, it may be difficult to secure a target level of strength and hardness.
The microstructure of the abrasion resistant steel in the present disclosure may further include bainite by 5 area% or less, and accordingly, low-temperature impact toughness may further improve. A fraction of martensite may more preferably be 96% or more, and even more preferably 97% or more. A fraction of bainite may more preferably be 4% or less, and even more Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 preferably 3% or less.
When the fraction of martensite is less than 95%, it may be difficult to secure a target level of strength and hardness.
The microstructure of the abrasion resistant steel in the present disclosure may further include bainite by 5 area% or less, and accordingly, low-temperature impact toughness may further improve. A fraction of martensite may more preferably be 96% or more, and even more preferably 97% or more. A fraction of bainite may more preferably be 4% or less, and even more Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 preferably 3% or less.
[0034] The abrasion resistant steel in the present disclosure provided as above may an effect of securing surface hardness of 550-650HB and also having an impact absorption energy of 21J
or more at a low temperature of -40 C. HB indicates surface hardness of the steel measured by the Brinell hardness tester.
or more at a low temperature of -40 C. HB indicates surface hardness of the steel measured by the Brinell hardness tester.
[0035] Also, it may be preferable that hardness (HB) and impact absorption energy (J) of the abrasion resistant steel in the present disclosure satisfy relational expression 2 as below.
In the present disclosure, low-temperature toughness properties may improve in addition to high hardness, and to this end, it may be preferable to satisfy relational expression 2 as below. In other words, when only surface hardness is high and impact toughness is degraded such that relational expression 2 is not satisfied, or when impact toughness is excellent but surface hardness does not reach a target value such that relational expression 2 is not satisfied, final target high hardness and low temperature toughness properties may not be guaranteed.
In the present disclosure, low-temperature toughness properties may improve in addition to high hardness, and to this end, it may be preferable to satisfy relational expression 2 as below. In other words, when only surface hardness is high and impact toughness is degraded such that relational expression 2 is not satisfied, or when impact toughness is excellent but surface hardness does not reach a target value such that relational expression 2 is not satisfied, final target high hardness and low temperature toughness properties may not be guaranteed.
[0036] [Relational Expression 2] HB+J 31.0 (HE
indicates surface hardness of the steel measured by the Brinell hardness tester, and J indicates an impact absorption energy value at -40 C)
indicates surface hardness of the steel measured by the Brinell hardness tester, and J indicates an impact absorption energy value at -40 C)
[0037] Hereinafter, a method of manufacturing the abrasion resistant steel will be described in detail.
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16
[0038] First, a steel slab may be heated in the temperature range of 1050-1250 C. When the slab heating temperature is less than 1050 C, re-solid solution of Nb may not be sufficient, whereas when the temperature exceeds 1250 C, austenite crystal grains may be coarsen such that a non-uniform structure may be formed. Therefore, in the present disclosure, the heating temperature of the steel slab may have a range of 1050-1250 C
preferably. A lower limit of the heating temperature of the steel slab may more preferably be 1060 C, even more preferably 1070 C, and most preferably 1080 C. An upper limit of the heating temperature of the steel slab may more preferably be 1230 C, even more preferably 1200 C, and most preferably 1180 C.
preferably. A lower limit of the heating temperature of the steel slab may more preferably be 1060 C, even more preferably 1070 C, and most preferably 1080 C. An upper limit of the heating temperature of the steel slab may more preferably be 1230 C, even more preferably 1200 C, and most preferably 1180 C.
[0039] The reheated steel slab may be roughly rolled in a temperature range of 950-1050 C to obtain a rough-rolled bar.
When the temperature is less than 950 C during the rough-rolling, a rolling load may increase and the pressure may be relatively weakened, such that deformation may not be sufficiently transmitted to a center of the slab in a thickness direction, and defects such as voids may not be removed. When the temperature exceeds 1050 C, recrystallization may simultaneously occur while rolling, and grains may grow, such that initial austenite grains may become excessively coarse.
Therefore, in the present disclosure, the rough-rolling temperature may preferably be 950-1050 C. A lower limit of the Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 rough-rolling temperature may more preferably be 960 C, even more preferably 970 C, and most preferably 980 C. An upper limit of the rough-rolling temperature may more preferably be 1040 C, even more preferably 1020 C, and most preferably 1000 C.
When the temperature is less than 950 C during the rough-rolling, a rolling load may increase and the pressure may be relatively weakened, such that deformation may not be sufficiently transmitted to a center of the slab in a thickness direction, and defects such as voids may not be removed. When the temperature exceeds 1050 C, recrystallization may simultaneously occur while rolling, and grains may grow, such that initial austenite grains may become excessively coarse.
Therefore, in the present disclosure, the rough-rolling temperature may preferably be 950-1050 C. A lower limit of the Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 rough-rolling temperature may more preferably be 960 C, even more preferably 970 C, and most preferably 980 C. An upper limit of the rough-rolling temperature may more preferably be 1040 C, even more preferably 1020 C, and most preferably 1000 C.
[0040] The rough-rolled bar may be finishing hot-rolled in a temperature range of 850-950 C to obtain a hot-rolled steel sheet. When the finishing hot-rolling temperature is less than 850 C, the rolling may become two-phase rolling, such that ferrite may be formed in the microstructure. When the temperature exceeds 950 C, a grain size of the final structure may become coarse such that low-temperature toughness may be deteriorated. Therefore, in the present disclosure, the finishing hot-rolling temperature may be 850-950 C preferably.
A lower limit of the finishing hot-rolling temperature may more preferably be 860 C, even more preferably 870 C, and most preferably 880 C. An upper limit of the finish hot-rolling temperature may more preferably be 940 C, even more preferably 930 C, and most preferably 920 C.
A lower limit of the finishing hot-rolling temperature may more preferably be 860 C, even more preferably 870 C, and most preferably 880 C. An upper limit of the finish hot-rolling temperature may more preferably be 940 C, even more preferably 930 C, and most preferably 920 C.
[0041] Thereafter, the hot-rolled steel sheet may be air-cooled to room temperature, and may be reheated in a temperature range of 860-950 C for a residence time of 1.3t+10min-1.3t+60m1n (t: sheet thickness) . The reheating may be performed for reverse transformation of the hot-rolled steel sheet including ferrite and pearlite into austenite single phase. When the reheating temperature is less than 860 C, Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 austenitization may not be sufficiently performed and coarse soft ferrites may be mixed, such that hardness of the final product may degrade. When the temperature exceeds 950 C, austenite grains may become coarse, such that hardenability may increase, but low temperature toughness of the steel may be deteriorated. Therefore, in the present disclosure, the reheating temperature may preferably be 860-950 C. A lower limit of the reheating temperature may more preferably be 870 C, even more preferably 880 C, and most preferably 890 C. An upper limit of the reheating temperature may more preferably be 940 C, even more preferably 930 C, and most preferably 920 C.
[0042] When the residence time during the reheating is less than 1.3t+10 minutes (t: sheet thickness) , austenitization may not occur sufficiently, such that a phase transformation by rapid cooling subsequently performed, a martensitic structure, may not be sufficiently obtained. When the residence time during the reheating exceeds 1.3t+60 minutes (t: sheet thickness) , austenite crystal grains may become coarse such that hardenability may increase, but low temperature toughness may deteriorate. Therefore, in the present disclosure, the residence time during the reheating may preferably be 1.3t+10min-1.3t+60m1n (t: sheet thickness) . A lower limit of the residence time during reheating may more preferably be 1.3t+12 minutes, even more preferably 1.3t+15 minutes, and most preferably 1.3t+20 minutes. An upper limit of the residence time Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 during reheating may more preferably be 1.3t+50min, even more preferably 1.3t+45min, and most preferably 1.3t+40m1n.
[0043] Thereafter, the reheated hot-rolled steel sheet may be water-cooled to 150 C or less with reference to a surface layer portion (e.g., the area from the surface to 1/8t (t: sheet thickness (mm) ) of the sheet. The water-cooling stop temperature exceeds 150 C, a ferrite phase may be formed during cooling or a bainite phase may be excessively formed. Therefore, the water-cooling stop temperature may preferably be 150 C or less. The water-cooling stop temperature may more preferably be 100 C or less, even more preferably 70 C or less, and most preferably 40 C or less.
[0044] The water-cooling rate may preferably be 10 C/s or more.
When the cooling rate is less than 1 0 C/s, a ferrite phase may be formed during cooling or a bainite phase may be excessively formed. A cooling rate during the water-cooling may more preferably be 15 C/s or more, and even more preferably 20 C/s or more. In the present disclosure, the higher the cooling rate, the more advantageous it may be, and thus, an upper limit of the cooling rate may not be particularly limited, and may be determined in consideration of facility limitations by a person skilled in the art.
When the cooling rate is less than 1 0 C/s, a ferrite phase may be formed during cooling or a bainite phase may be excessively formed. A cooling rate during the water-cooling may more preferably be 15 C/s or more, and even more preferably 20 C/s or more. In the present disclosure, the higher the cooling rate, the more advantageous it may be, and thus, an upper limit of the cooling rate may not be particularly limited, and may be determined in consideration of facility limitations by a person skilled in the art.
[0045] The hot-rolled steel sheet in the present disclosure having gone through the above process conditions may be a thick steel sheet having a thickness of 60mm or less, and may have Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 a thickness of 8-50mm more preferably, and 12-40mm even more preferably. In the present disclosure, it may be preferable to not perform a tempering process on the thick steel sheet.
Node for Invention]
Node for Invention]
[0046] Hereinafter, the present disclosure will be described in greater detail with reference to an embodiment. However, it should be noted that the following embodiment are provided to describe the present disclosure in greater detail, and to not limit the scope of the present disclosure. The scope of the present disclosure may be determined by matters described in the claims and matters reasonably inferred therefrom.
(Embodiment)
(Embodiment)
[0047] A steel slab having alloy compositions as in Tables 1 and 2 below was prepared, and the steel slab heating-rough-rolling-hot-rolling-cooling (room temperature)-reheating-water cooling was performed on the steel slab under the conditions as in Table 3 below to manufacture a hot-rolled steel sheet. A microstructure and mechanical properties of the hot-rolled steel sheet were measured, and results thereof are listed in Table 4 below.
[0048] In this case, as for the microstructure, the sample was cut out in an arbitrary size to manufacture a mirror surface, the surface was corroded using a nital etching solution, and a 1/2t position, a center of the thickness, was observed using an optical microscope and an electron scanning microscope.
Date Recue/Date Received 2021-03-16
Date Recue/Date Received 2021-03-16
[0049] Hardness and toughness were measured using the Brinell hardness tester (load 3000kgf, lOmm tungsten indentation) and the Charpy impact tester, respectively. As for surface hardness, an average value of values obtained by milling the sheet surface by 2 mm and measuring surface hardness three times therefrom was used. As for the Charpy impact test result, an average value of values obtained by taking a sample from a 1/4t position and measuring toughness three times therefrom at -40 C was used.
[0050] [Table 1 ALLOY COMPOSITION (WEIGHT%) CLASSIFICATION
Si Mn P S Al Cr Ni Mo B Co COUPARATIVE
0.346 0.35 3,07 0.013 0.0031 0.031 0.05 0,05 0,01 0,0011 -361FApRAT2IVE 0.287 0.38 0.85 0.009 0.0018 0.025 0.12 1,21 0.13 0.0002 -C0FA'Ar;tIVE 0.440 0.31 1.51 0.015 0.0016 0= .036 0.45 0.09 0.19 0.0015 - 0.01 C0N2EtIVE 0.385 0,25 0.85 0.007 0.0021 0.036 0.78 0.37 0.56 0.0017 0.01 IrlailrE 0.370 0.34 1.36 0.007 0.0010 0.023 0.58 0.92 0.25 0.0022 0.01 .77E-INsIE'.\E[ Dirf 0.401 0:31 1.23 0.008 - 0.0021 0.022 0.31 2:91 6.56 6.0020 0.01 -fliC1rC/E 0.383 0.21 1.47 0.008 0.0009 0.031 0,31 1.74 0.33 0.0020 0,01
Si Mn P S Al Cr Ni Mo B Co COUPARATIVE
0.346 0.35 3,07 0.013 0.0031 0.031 0.05 0,05 0,01 0,0011 -361FApRAT2IVE 0.287 0.38 0.85 0.009 0.0018 0.025 0.12 1,21 0.13 0.0002 -C0FA'Ar;tIVE 0.440 0.31 1.51 0.015 0.0016 0= .036 0.45 0.09 0.19 0.0015 - 0.01 C0N2EtIVE 0.385 0,25 0.85 0.007 0.0021 0.036 0.78 0.37 0.56 0.0017 0.01 IrlailrE 0.370 0.34 1.36 0.007 0.0010 0.023 0.58 0.92 0.25 0.0022 0.01 .77E-INsIE'.\E[ Dirf 0.401 0:31 1.23 0.008 - 0.0021 0.022 0.31 2:91 6.56 6.0020 0.01 -fliC1rC/E 0.383 0.21 1.47 0.008 0.0009 0.031 0,31 1.74 0.33 0.0020 0,01
[0051] [Table 2]
ALLOY COMPOSITION (WEIGHT%) CLASSIFICATION
Cu Ti Nb V Ca As - Sn w RELATIONAL
CITPFW,TIRE 0.05 0.013 0.021 0.03 0.0002 -0.017 COILI,PV2IVE 6.45 -- 0.018 0.037 0.01 - 0=
.0004 0.347 Ciihrr - 0.02 0.017 0.026 0.02 0= .0009 0.003 0.003 - 0.040 a 7 V7k. fiVE 0.21 0.002 0.023 0.03 0.0005 0.003 0.004 0.01 0.142 &EEL 1 1SENTIVE 0.31 0.016 0,035 0.04 0.0012 - 0.01 0.340 Igc.rpgpI\i2E 0.15 0.012 0.024 - 0.0006 0.003 0.003 0.01 1.167 IrI 0,22 0.013 - 0.04 0= .0004 0,003 0.003 0.666 [RELATIONAL EXPRESSION 1] [C] x[Ni]
ALLOY COMPOSITION (WEIGHT%) CLASSIFICATION
Cu Ti Nb V Ca As - Sn w RELATIONAL
CITPFW,TIRE 0.05 0.013 0.021 0.03 0.0002 -0.017 COILI,PV2IVE 6.45 -- 0.018 0.037 0.01 - 0=
.0004 0.347 Ciihrr - 0.02 0.017 0.026 0.02 0= .0009 0.003 0.003 - 0.040 a 7 V7k. fiVE 0.21 0.002 0.023 0.03 0.0005 0.003 0.004 0.01 0.142 &EEL 1 1SENTIVE 0.31 0.016 0,035 0.04 0.0012 - 0.01 0.340 Igc.rpgpI\i2E 0.15 0.012 0.024 - 0.0006 0.003 0.003 0.01 1.167 IrI 0,22 0.013 - 0.04 0= .0004 0,003 0.003 0.666 [RELATIONAL EXPRESSION 1] [C] x[Ni]
[0052] [Table 3]
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 STEEL TYPE SLAB ROUGH- FINISHING- REHEATING REHEATING
COOLING CMG - THICKNESS
No, HEATING ROLLING HOT- TEMPERATURE RESIDENCE RATE
TERMINATION
TEMPERATURE TEMPERATURE ROLLING TIME TEMPERATURE ( mm) CLASSIFICATION
( C) (.0 TEMPERATURE (CC) (MIN) (T/s) ( C) ( C) , COMPARA FIVE - 1121 1048 ' 901 908 32 52 42 12 126 ' 40 ' EXAMPLE 2 ,3TEEL I
EXAMPLE 3 , .
COMPARATIVE . 1= 133 - 1045 ' 903 921, 45 49 176 CgAAPU1/4FTE COMPARATIVE 1125 1021 911 921 52 48 52 30 EXAMPLE 6 , COMPARATIVE - 1= 123 1049 882 911 32 65 24 8 EXAMPLE 7 , , COMPARATIVE' COMPARATIVE 1097 ' 1038 - 901 ' 917 ' 71 COMPARATIVE 1145 1019 934 915 93 40 ' 123 50 ' COMPARATIVE COMPARATIVE 1112 1039 ¨ 930 ' 927 ' 77 ' 47 '135 ' 30 ' COMPARATIVE 1127 1044 947 928 ' 1.13 25 27 60 INVENTIVE 1124 1031 ' 888 918 52 53 126 12 EXAMPLE
' INVENTIVE 1131 1039 915 915 61 ' 50 53 20 ' EXAMPLE 2 STEEL 1 , COMPARATIVE - 1= 129 ' 1045 . 920 910 78 50 200 EXAMPLE 14 , INVENTIVE ' INVENTIVE 1137 1042 931 913 93 44 25 40 EgD-I STEEL 2 , 1102 1041 946 920 88 33 36 50 ' EXAMPLE 4 .
INVENTIVE 1105 1044 932 916 116 28 141 ' 60
Date Recue/Date Received 2021-03-16 CA 031.13056 2021-03-16 STEEL TYPE SLAB ROUGH- FINISHING- REHEATING REHEATING
COOLING CMG - THICKNESS
No, HEATING ROLLING HOT- TEMPERATURE RESIDENCE RATE
TERMINATION
TEMPERATURE TEMPERATURE ROLLING TIME TEMPERATURE ( mm) CLASSIFICATION
( C) (.0 TEMPERATURE (CC) (MIN) (T/s) ( C) ( C) , COMPARA FIVE - 1121 1048 ' 901 908 32 52 42 12 126 ' 40 ' EXAMPLE 2 ,3TEEL I
EXAMPLE 3 , .
COMPARATIVE . 1= 133 - 1045 ' 903 921, 45 49 176 CgAAPU1/4FTE COMPARATIVE 1125 1021 911 921 52 48 52 30 EXAMPLE 6 , COMPARATIVE - 1= 123 1049 882 911 32 65 24 8 EXAMPLE 7 , , COMPARATIVE' COMPARATIVE 1097 ' 1038 - 901 ' 917 ' 71 COMPARATIVE 1145 1019 934 915 93 40 ' 123 50 ' COMPARATIVE COMPARATIVE 1112 1039 ¨ 930 ' 927 ' 77 ' 47 '135 ' 30 ' COMPARATIVE 1127 1044 947 928 ' 1.13 25 27 60 INVENTIVE 1124 1031 ' 888 918 52 53 126 12 EXAMPLE
' INVENTIVE 1131 1039 915 915 61 ' 50 53 20 ' EXAMPLE 2 STEEL 1 , COMPARATIVE - 1= 129 ' 1045 . 920 910 78 50 200 EXAMPLE 14 , INVENTIVE ' INVENTIVE 1137 1042 931 913 93 44 25 40 EgD-I STEEL 2 , 1102 1041 946 920 88 33 36 50 ' EXAMPLE 4 .
INVENTIVE 1105 1044 932 916 116 28 141 ' 60
[0053] [Table 4]
Date Recue/Date Received 2021-03-16 MICROSTRUCTURE (AREA%) SURFACE IMPACT TOUGHNESS RELATIONAL
__________________________________________________________________ HARDNESS
CLASSIFICATION M THE OTHERS (HB) (J, @-40 C) COMPARATIVE 100 - 589 7 84.1 COMPARATIVE 95 B:5% 592 5 118.4 CRAVE 100 - 574 8 71.8 CgAPMAPRIAET1E 94 B:6% 541 34 15.9 COMPARATIVE 97 B:3% 529 38 13.9 C8 '"WE 98 B:2% 545 31 17.6 CV\WRIAckE 100 - 670 6 111.7 CRipmAiUrkE 100 - 667 _______ 5 133.4 HARE 99 R:1% 662 5 132.4 AMWE 100 - 619 11 ________ 56.3 CfbiSPWE 96 B:4% 609 19 32.1 COMPARATIVE 100 - 623 12 51.9 Ep_D,IIIV2 99 B:1% 608 25 24.3 WrhU 100 - 605 27 ________ 22,4 COMPARATIVE 85 B:10%, PF:5% 516 48 10.8 OikrkTP E 90 B:6%, RA:4% 531 75 7.1 100 - 625 35 17.9 VITIQ 100 - 630 33 ________ 19.1 INVENTIVE 98 B:2% 618 42 14.7 CRAr-ijAi& 75 B:25% 411 63 6.5 EalAt5 96 B:4% 604 45 13.4 [ RELATIONAL EXPRESSION 2] 11B J (HB INDICATES SURFACE HARDNESS OF THE STEEL
MEASURED BY
THE BRINELL HARDNESS TESTER, AND J INDICATES AN IMPACT ABSORPTION ENERGY VALUE
AT -40 C.) IC MARTENSITE , B: BAINITE , PF: POLYGONAL FERRITE, RA: RETAINED AUSTENITE
Date Recue/Date Received 2021-03-16 MICROSTRUCTURE (AREA%) SURFACE IMPACT TOUGHNESS RELATIONAL
__________________________________________________________________ HARDNESS
CLASSIFICATION M THE OTHERS (HB) (J, @-40 C) COMPARATIVE 100 - 589 7 84.1 COMPARATIVE 95 B:5% 592 5 118.4 CRAVE 100 - 574 8 71.8 CgAPMAPRIAET1E 94 B:6% 541 34 15.9 COMPARATIVE 97 B:3% 529 38 13.9 C8 '"WE 98 B:2% 545 31 17.6 CV\WRIAckE 100 - 670 6 111.7 CRipmAiUrkE 100 - 667 _______ 5 133.4 HARE 99 R:1% 662 5 132.4 AMWE 100 - 619 11 ________ 56.3 CfbiSPWE 96 B:4% 609 19 32.1 COMPARATIVE 100 - 623 12 51.9 Ep_D,IIIV2 99 B:1% 608 25 24.3 WrhU 100 - 605 27 ________ 22,4 COMPARATIVE 85 B:10%, PF:5% 516 48 10.8 OikrkTP E 90 B:6%, RA:4% 531 75 7.1 100 - 625 35 17.9 VITIQ 100 - 630 33 ________ 19.1 INVENTIVE 98 B:2% 618 42 14.7 CRAr-ijAi& 75 B:25% 411 63 6.5 EalAt5 96 B:4% 604 45 13.4 [ RELATIONAL EXPRESSION 2] 11B J (HB INDICATES SURFACE HARDNESS OF THE STEEL
MEASURED BY
THE BRINELL HARDNESS TESTER, AND J INDICATES AN IMPACT ABSORPTION ENERGY VALUE
AT -40 C.) IC MARTENSITE , B: BAINITE , PF: POLYGONAL FERRITE, RA: RETAINED AUSTENITE
[0054] As indicated in Tables 1 to 4, inventive examples 1 to 6 satisfying the alloy composition, relational expression 1, and the manufacturing conditions suggested in the present disclosure satisfied the microstructure fraction of the present disclosure, and secured excellent hardness and low-temperature impact toughness.
[0055] It is indicated that comparative examples 1 to 12, which Date Recue/Date Received 2021-03-16 satisfied the manufacturing conditions suggested in the present disclosure but did not satisfy the alloy composition or relational expression 1, did not satisfy hardness and low-temperature impact toughness aimed in the present disclosure.
[0056] It is indicated that comparative example 13 satisfying the alloy composition and relational expression 1 suggested in the present disclosure but not satisfying the reheating temperature among the manufacturing conditions did not secure the microstructure type and fraction suggested in the present disclosure, and surface hardness was low.
[0057] It is indicated that comparative example 14 satisfying the alloy composition and relational expression 1 suggested in the present disclosure but not satisfying the cooling termination temperature among the manufacturing conditions secured the martensite fraction suggested in the present disclosure, but retained austenite was formed, and accordingly, surface hardness was low.
[0058] It is indicated that comparative example 15 satisfying the alloy composition and relational expression 1 suggested in the present disclosure but not satisfying the cooling rate among the manufacturing conditions did not secure the martensite fraction suggested in the present disclosure, and accordingly, surface hardness was low.
***
***
[0059] In some aspects, embodiments of the present invention as described herein include the following items:
Date Regue/Date Received 2022-08-23 [Item 1]
An abrasion resistant steel having excellent hardness and impact toughness, consisting of:
by weight%, 0.33-0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.022-0.07% of aluminum (Al), 0.55-5.0% of nickel (Ni), 0 .01-1 .5% of copper (Cu), 0 .01-0 .8% of chromium (Cr), 0.01-0.8%
of molybdenum (Mo), 2-50 ppm of boron (B), . 001-0 .02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding 0), 0.05% or less of tin (Sn) (excluding 0) , and 0.05% or less of tungsten (W) (excluding 0) , with a balance of Fe and other inevitable impurities, wherein C and Ni satisfy relational expression 1 as below, wherein a microstructure includes 95-99 area% of martensite and 1-5% of bainite, and wherein the abrasion resistant steel secures hardness of 550-650HB, and has 21J or more at a low temperature of -40 C, where HB is surface hardness of the steel measured by the Brinell hardness tester, [Relational Expression 1] [C]x [Ni] 0.231.
[Item 2]
The abrasion resistant steel of item 1, wherein the Date Recue/Date Received 2023-05-30 abrasion resistant steel has hardness (HB) and impact absorption energy (J) satisfying relational expression 2 as below, [Relational Expression 2] HB+J 31.0, where HR is surface hardness of the steel measured by the Brinell hardness tester, and J is an impact absorption energy value at -40 C.
[Item 3]
The abrasion resistant steel of item 1 or 2, wherein the abrasion resistant steel has a thickness of 60 mm or less.
[Item 4]
A method of manufacturing the abrasion resistant steel of item 1 having excellent hardness and impact toughness, the method comprising:
heating a steel slab consisting of, by weight%, 0.33-0.42%
of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0) , 0.02% or less of sulfur (S) (excluding 0) , 0.022-0.07% of aluminum (Al), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8%
of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 2-50 ppm of boron (B), 0.001-0.02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% of niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding Date Recue/Date Received 2023-05-30 0), 0.05% or less of tin (Sn) (excluding 0), and 0.05% or less of tungsten (W) (excluding 0), with a balance of Fe and other inevitable impurities, where C and Ni satisfy relational expression 1 as below, in a temperature range of 1050-1250 C;
obtaining a rough-rolled bar by rough-rolling the heated steel slab in a temperature range of 950-1050 C;
obtaining a hot-rolled steel sheet by finishing-hot-rolling the rough-rolled bar in a temperature range of 850-950 C;
air-cooling the hot-rolled steel sheet to room temperature and reheating the steel sheet for a maintaining time of 1.3t+10min-1.3t+60min (t: sheet thickness) in a temperature range of 860-950 C; and water-cooling the reheated hot-rolled steel sheet to 150 C or less, [Relational Expression 1] [C]x[Ni] 0.231.
[Item 5]
The method of item 4, wherein a cooling rate is 10 C/s or more in the water-cooling.
Date Recue/Date Received 2023-05-30
Date Regue/Date Received 2022-08-23 [Item 1]
An abrasion resistant steel having excellent hardness and impact toughness, consisting of:
by weight%, 0.33-0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.022-0.07% of aluminum (Al), 0.55-5.0% of nickel (Ni), 0 .01-1 .5% of copper (Cu), 0 .01-0 .8% of chromium (Cr), 0.01-0.8%
of molybdenum (Mo), 2-50 ppm of boron (B), . 001-0 .02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding 0), 0.05% or less of tin (Sn) (excluding 0) , and 0.05% or less of tungsten (W) (excluding 0) , with a balance of Fe and other inevitable impurities, wherein C and Ni satisfy relational expression 1 as below, wherein a microstructure includes 95-99 area% of martensite and 1-5% of bainite, and wherein the abrasion resistant steel secures hardness of 550-650HB, and has 21J or more at a low temperature of -40 C, where HB is surface hardness of the steel measured by the Brinell hardness tester, [Relational Expression 1] [C]x [Ni] 0.231.
[Item 2]
The abrasion resistant steel of item 1, wherein the Date Recue/Date Received 2023-05-30 abrasion resistant steel has hardness (HB) and impact absorption energy (J) satisfying relational expression 2 as below, [Relational Expression 2] HB+J 31.0, where HR is surface hardness of the steel measured by the Brinell hardness tester, and J is an impact absorption energy value at -40 C.
[Item 3]
The abrasion resistant steel of item 1 or 2, wherein the abrasion resistant steel has a thickness of 60 mm or less.
[Item 4]
A method of manufacturing the abrasion resistant steel of item 1 having excellent hardness and impact toughness, the method comprising:
heating a steel slab consisting of, by weight%, 0.33-0.42%
of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0) , 0.02% or less of sulfur (S) (excluding 0) , 0.022-0.07% of aluminum (Al), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8%
of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 2-50 ppm of boron (B), 0.001-0.02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% of niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding Date Recue/Date Received 2023-05-30 0), 0.05% or less of tin (Sn) (excluding 0), and 0.05% or less of tungsten (W) (excluding 0), with a balance of Fe and other inevitable impurities, where C and Ni satisfy relational expression 1 as below, in a temperature range of 1050-1250 C;
obtaining a rough-rolled bar by rough-rolling the heated steel slab in a temperature range of 950-1050 C;
obtaining a hot-rolled steel sheet by finishing-hot-rolling the rough-rolled bar in a temperature range of 850-950 C;
air-cooling the hot-rolled steel sheet to room temperature and reheating the steel sheet for a maintaining time of 1.3t+10min-1.3t+60min (t: sheet thickness) in a temperature range of 860-950 C; and water-cooling the reheated hot-rolled steel sheet to 150 C or less, [Relational Expression 1] [C]x[Ni] 0.231.
[Item 5]
The method of item 4, wherein a cooling rate is 10 C/s or more in the water-cooling.
Date Recue/Date Received 2023-05-30
Claims (5)
- [Claim 1]
An abrasion resistant steel having excellent hardness and impact toughness, consisting of:
by weight%, 0.33-0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.022-0.07% of aluminum (Al), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8% of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 2-50 ppm of boron (B), 0.001-0.02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding 0), 0.05% or less of tin (Sn) (excluding 0), and 0.05% or less of tungsten (W) (excluding 0), with a balance of Fe and other inevitable impurities, wherein C and Ni satisfy relational expression 1 as below, wherein a microstructure includes 95-99 area% of martensite and 1-5% of bainite, and wherein the abrasion resistant steel secures hardness of 550-650HB, and has 21J or more at a low temperature of -Date Recue/Date Received 2023-05-30 40 C, where HB is surface hardness of the steel measured by the Brinell hardness tester, [Relational Expression 1] [C]x[Ni] 0.231. - [Claim 2]
The abrasion resistant steel of claim 1, wherein the abrasion resistant steel has hardness (HB) and impact absorption energy (J) satisfying relational expression 2 as below, [Relational Expression 2] HB+J 31.0, where HB is surface hardness of the steel measured by the Brinell hardness tester, and J is an impact absorption energy value at -40 C. - [Claim 3]
The abrasion resistant steel of claim 1 or 2, wherein the abrasion resistant steel has a thickness of 60 mm or less. - [Claim 4]
A method of manufacturing the abrasion resistant steel of claim 1 having excellent hardness and impact toughness, the method comprising:
heating a steel slab consisting of, by weight%, 0.33-Date Recue/Date Received 2023-05-30 0.42% of carbon (C), 0.1-0.7% of silicon (Si), 0.6-1.6% of manganese (Mn), 0.05% or less of phosphorus (P) (excluding 0), 0.02% or less of sulfur (S) (excluding 0), 0.022-0.07%
of aluminum (Al), 0.55-5.0% of nickel (Ni), 0.01-1.5% of copper (Cu), 0.01-0.8% of chromium (Cr), 0.01-0.8% of molybdenum (Mo), 2-50 ppm of boron (B), 0.001-0.02% of cobalt (Co), 0.005-0.02% of titanium (Ti), 2-100 ppm of calcium (Ca) and further comprising one or two of 0.002-0.05% of niobium (Nb) and 0.002-0.05% of vanadium (V), optionally further comprising one or more selected from the group consisting of 0.05% or less of arsenic (As) (excluding 0), 0.05% or less of tin (Sn) (excluding 0), and 0.05% or less of tungsten (W) (excluding 0), with a balance of Fe and other inevitable impurities, where C and Ni satisfy relational expression 1 as below, in a temperature range of 1050-1250 C;
obtaining a rough-rolled bar by rough-rolling the heated steel slab in a temperature range of 950-1050 C;
obtaining a hot-rolled steel sheet by finishing-hot-rolling the rough-rolled bar in a temperature range of 850-950 C;
air-cooling the hot-rolled steel sheet to room temperature and reheating the steel sheet for a maintaining time of 1.3t+10min-1.3t+60min (t: sheet thickness) in a temperature range of 860-950 C; and Date Recue/Date Received 2023-05-30 water-cooling the reheated hot-rolled steel sheet to 150 C or less, [Relational Expression 1] [C]x[Ni] 0.231. - [Claim 5]
The method of claim 4, wherein a cooling rate is C/s or more in the water-cooling.
Date Recue/Date Received 2023-05-30
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KR1020180115164A KR102175570B1 (en) | 2018-09-27 | 2018-09-27 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
KR10-2018-0115164 | 2018-09-27 | ||
PCT/KR2019/012325 WO2020067686A1 (en) | 2018-09-27 | 2019-09-23 | Abrasion resistant steel having excellent hardness and impact toughness, and manufacturing method therefor |
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KR102498144B1 (en) * | 2020-12-18 | 2023-02-08 | 주식회사 포스코 | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof |
KR102498142B1 (en) * | 2020-12-18 | 2023-02-08 | 주식회사 포스코 | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof |
WO2023073406A1 (en) * | 2021-10-28 | 2023-05-04 | Arcelormittal | Hot rolled and steel sheet and a method of manufacturing thereof |
KR102474002B1 (en) * | 2021-11-23 | 2022-12-05 | 대동중공업주식회사 | To improve abrasion resistance, a ribbon screw of a horizontal mixer that's hard-paced |
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