EP4265785A1 - High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same - Google Patents
High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same Download PDFInfo
- Publication number
- EP4265785A1 EP4265785A1 EP21906840.0A EP21906840A EP4265785A1 EP 4265785 A1 EP4265785 A1 EP 4265785A1 EP 21906840 A EP21906840 A EP 21906840A EP 4265785 A1 EP4265785 A1 EP 4265785A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- bullet
- hardness
- less
- excellent low
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 128
- 239000010959 steel Substances 0.000 title claims abstract description 128
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 28
- 238000000034 method Methods 0.000 title abstract description 18
- 238000010438 heat treatment Methods 0.000 claims description 49
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 44
- 239000011651 chromium Substances 0.000 claims description 28
- 239000011572 manganese Substances 0.000 claims description 27
- 238000001816 cooling Methods 0.000 claims description 24
- 229910001566 austenite Inorganic materials 0.000 claims description 23
- 239000011575 calcium Substances 0.000 claims description 23
- 239000010936 titanium Substances 0.000 claims description 23
- 239000010955 niobium Substances 0.000 claims description 22
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 19
- 229910052710 silicon Inorganic materials 0.000 claims description 19
- 239000010703 silicon Substances 0.000 claims description 19
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 18
- 229910052799 carbon Inorganic materials 0.000 claims description 18
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 17
- 229910000734 martensite Inorganic materials 0.000 claims description 16
- 238000005096 rolling process Methods 0.000 claims description 15
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 14
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 14
- 229910052796 boron Inorganic materials 0.000 claims description 14
- 229910052804 chromium Inorganic materials 0.000 claims description 14
- 229910052759 nickel Inorganic materials 0.000 claims description 14
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 13
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 13
- 229910052748 manganese Inorganic materials 0.000 claims description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims description 13
- 239000011733 molybdenum Substances 0.000 claims description 13
- 230000000717 retained effect Effects 0.000 claims description 13
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 12
- 229910052719 titanium Inorganic materials 0.000 claims description 12
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 11
- 229910052782 aluminium Inorganic materials 0.000 claims description 11
- 229910052758 niobium Inorganic materials 0.000 claims description 11
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 11
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 10
- 229910052791 calcium Inorganic materials 0.000 claims description 10
- 229910052757 nitrogen Inorganic materials 0.000 claims description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 9
- 229910052717 sulfur Inorganic materials 0.000 claims description 9
- 239000011593 sulfur Substances 0.000 claims description 9
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 8
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 239000011574 phosphorus Substances 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 6
- 238000010521 absorption reaction Methods 0.000 claims description 5
- 239000000463 material Substances 0.000 description 21
- 239000000203 mixture Substances 0.000 description 19
- 229910045601 alloy Inorganic materials 0.000 description 18
- 239000000956 alloy Substances 0.000 description 18
- 230000000694 effects Effects 0.000 description 18
- 238000005496 tempering Methods 0.000 description 18
- 230000000171 quenching effect Effects 0.000 description 15
- 230000002349 favourable effect Effects 0.000 description 9
- 230000000704 physical effect Effects 0.000 description 9
- 230000008569 process Effects 0.000 description 9
- 238000010791 quenching Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 229910001563 bainite Inorganic materials 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000001747 exhibiting effect Effects 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000004148 curcumin Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005457 optimization Methods 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
- 230000000149 penetrating effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
- 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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- 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
- C21D1/26—Methods of annealing
-
- 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
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- 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
- C22C38/54—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
- C21D2211/001—Austenite
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
Definitions
- the present disclosure relates to a material appropriate for armored vehicles, explosion-proof structures, and the like, and more particularly to bullet-proof steel having excellent low-temperature impact toughness and having high hardness, and a method for manufacturing the same.
- Bullet-proof steel is a material of which a surface is made very hard for its main function of blocking bullets, and is used where protection is required, such as for an exterior of armored vehicles used on the battlefield. Since bulletproof performance is directly related to human life, research to improve the performance of bulletproof materials has been actively conducted in the past, and recently, a non-ferrous material such as titanium and aluminum has been developed.
- the non-ferrous material has an advantage of weight reduction compared to a steel material, but is relatively expensive and has poor workability. As compared to the non-ferrous material, since the steel material is relatively inexpensive and may change physical properties such as harness relatively easily, the steel material is widely used as a material for self-propelled artillery, wheeled armored vehicles, and the like.
- Hardness is one of the most important physical properties for securing the performance of bullet-proof steel, but simple high hardness does not guarantee bulletproof performance.
- a high hardness characteristic is a factor that increases resistance to bullets penetrating through a material, but the material having high hardness may be relatively easily broken, so the high hardness characteristic cannot necessarily guarantee excellent bulletproof performance. Therefore, there is a need to develop a material that can simultaneously secure brittle fracture resistance to external impact as well as high hardness characteristics rather than simply promoting high hardness of the material.
- Patent Document Korean Patent Publication No. 10-2018-0043788 (published on April 30, 2018 )
- An aspect of the present disclosure is to provide bullet-proof steel having high hardness characteristics and excellent low-temperature impact toughness and a method for manufacturing the same.
- An object of the present disclosure is not limited to the above description.
- the object of the present disclosure will be understood from the entire content of the present specification, and a person skilled in the art to which the present disclosure pertains will understand an additional object of the present disclosure without difficulty.
- Mn manga
- [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel sheet, and 0 is substituted when the corresponding element is not intentionally added.
- the bullet-proof steel may further include, by weight: at least one of 0.005 to 0.025% of titanium (Ti) and 0.2% or less of vanadium (V).
- a fraction of the tempered martensite may be 90% or more by area, and a fraction of the retained austenite may be 0.5% by area to 5% by area.
- the bullet-proof steel may have a surface hardness of 360 to 440 HB, and an impact absorption energy of 27 J or more at -40°C.
- the bullet-proof steel may have a thickness of 5 to 20 mm.
- a manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness includes operations of: preparing a steel slab including, by weight: 0.18 to 0.25% of carbon (C), 1.0 to 2.0% of silicon (Si), 0.5 to 1.6% of manganese (Mn), 0.5 to 1.2% of nickel (Ni), 0.4 to 1.5% of chromium (Cr), 0.05% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.006% or less of nitrogen (N), 0.07% or less of aluminum (Al) (excluding 0%), 0.1 to 0.5% of molybdenum (Mo), 0.01 to 0.05% of niobium (Nb), 0.0002 to 0.005% of boron (B), 0.0005 to 0.004% of calcium (Ca), with a balance of iron (Fe) and inevitable impurities, satisfying the following [Relational Expression 1]; heating the steel slab in a temperature range of 1050 to 12
- [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel slab, and 0 is substituted when the corresponding element is not intentionally added.
- the steel slab may further include, by weight: at least one of 0.005 to 0.025% of titanium (Ti) and 0.2% or less of vanadium (V).
- a residence time during the first heat treatment may be 1.3t * 10 minutes (t: plate thickness (mm)) or more.
- a holding time during the secondary heat treatment may be 1.9t+10 minutes (t: plate thickness (mm)) or more.
- bullet-proof steel having excellent low-temperature toughness while having ultra-high hardness may be provided.
- the present disclosure may provide bullet-proof steel having a target level of physical properties without performing a further heat treatment from optimization of alloy compositions and manufacturing conditions, and thus, is economically favorable.
- the present disclosure relates to a high-hardness bullet-proof steel having excellent low-temperature impact toughness and a method for manufacturing the same .
- preferred embodiments of the present disclosure will be described. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to the embodiments described below. The present embodiments are provided to those skilled in the art to further elaborate the present disclosure.
- the present inventors have studied in depth, in order to provide a steel material having excellent physical properties such as high hardness characteristics, low-temperature impact toughness, and the like, which are essentially required physical properties, as a material which may be appropriately applied to tracked armored vehicles, explosion-proof structures, and the like.
- the bulletproof performance of the steel material was intended to be improved by an economically favorable method, and thus, the present disclosure was provided.
- % represents a content of each element based on weight, unless otherwise particularly specified.
- Carbon (C) is an element which is effective for improving strength and hardness in steel having a low-temperature transformation phase such as a martensite or bainite phase, and is effective for improving hardenability. In order to sufficiently obtain the effect described above, 0.18% or more of carbon (C) may be included. Preferably, a lower limit of a content of carbon (C) may be 0.19%, and more preferably, the lower limit of the content of carbon (C) may be 0.20%. However, when carbon (C) is excessively added, there may be a concern that weldability and toughness of steel are deteriorated, so in the present disclosure, an upper limit of the content of carbon (C) may be limited to 0.25%. Preferably, the upper limit of the content of carbon (C) may be 0.24%.
- Silicon (Si) is an element which is effective for improving strength due to solid solution strengthening together with a deoxidation effect, and is also an element suppressing formation of carbides such as cementite in a steel material containing a certain amount or more of C to promote production of residual austenite.
- carbides such as cementite
- a steel material containing a certain amount or more of C may be included.
- silicon (Si) may be included.
- a lower limit of a content of silicon (Si) may be 1.1%, and more preferably, the lower limit of the content of silicon (Si) may be 1.2%.
- an upper limit of the content of silicon (Si) may be limited to 2.0%.
- the upper limit of the content of silicon (Si) may be 1.9%, and more preferably, the upper limit of the content of silicon (Si) may be 1.8%.
- Manganese (Mn) is an element favorable to suppress production of ferrite and lower an Ar3 temperature, thereby improving quenching properties of steel to increase strength and toughness.
- 0.5% or more of manganese (Mn) may be included.
- a lower limit of a content of manganese (Mn) may be 0.6%, and more preferably, the lower limit of the content of manganese (Mn) may be 0.7%.
- an upper limit of the content of manganese (Mn) may be limited to 1.6%.
- the upper limit of the content of manganese (Mn) may be 1.5%, and more preferably, the upper limit of the content of manganese (Mn) may be 1.45%.
- Nickel (Ni) is an element favorable to improve both strength and toughness of steel. In order to obtain the effect described above, in the present disclosure, 0.5% or more of nickel (Ni) may be included. Preferably, a lower limit of a content of nickel (Ni) may be 0.6%, and more preferably, the lower limit of the content of nickel (Ni) may be 0.7%. However, nickel (Ni) is an expensive element, when nickel (Ni) is excessively added, manufacturing costs may be greatly increased, so in the present disclosure, an upper limit of the content of nickel (Ni) may be limited to 1.2%. Preferably, the upper limit of the content of nickel (Ni) may be 1.17%, and more preferably, the upper limit of the content of nickel (Ni) may be 1.15%.
- Chromium (Cr) is an element of increasing quenching properties of steel to improve strength, and effectively contributing to securing hardness in a surface part and a center part of steel.
- Cr chromium
- Cr is also an element for economically securing hardness and toughness.
- 0.4% or more of chromium (Cr) may be included.
- a lower limit of a content of chromium (Cr) may be 0.45%.
- an upper limit of the content of chromium (Cr) may be limited to 1.5%.
- the upper limit of the content of chromium (Cr) may be 1.4%, and more preferably, the upper limit of the content of chromium (Cr) may be 1.3%.
- Phosphorous (P) 0.05% or less
- Phosphorus (P) is an element which is inevitably contained in steel, and is also an element which deteriorates toughness of the steel. Thus, it is preferred to lower a content of P as much as possible.
- an upper limit of the content of phosphorus (P) may be limited to 0.05%. More favorably, the content thereof may be limited to 0.03% or less. However, 0% may be excluded considering an inevitably contained level.
- Sulfur (S) is an element which is inevitably contained in steel, and is also an element forming MnS inclusions to deteriorate toughness of steel. Thus, it is preferred to lower a content of S as much as possible.
- an upper limit of the content of sulfur (S) may be limited to 0.02%. More favorably, the content thereof may be limited to 0.01% or less. However, 0% may be excluded considering an inevitably contained level.
- Nitrogen (N) is an element which is favorable to improve strength of steel by forming precipitates in steel, but when a content of nitrogen (N) is more than a certain level, which may rather cause deterioration in toughness of steel.
- an upper limit of a content of nitrogen (N) may be limited to 0.006%. However, 0% may be excluded considering an inevitably contained level.
- Aluminum (Al) is an element effective for lowering an oxygen content in molten steel as a deoxidizing agent of steel. However, when aluminum (Al) is excessively added, cleanliness of steel may be impaired, so in the present disclosure, an upper limit of a content of aluminum (Al) may be limited to 0.07%.
- Molybdenum (Mo) is an element favorable to increase quenching properties of steel, and in particular, to improve hardness of a thick material having a certain thickness or more. In order to obtain the effect described above, in the present disclosure, 0.1% or more of molybdenum (Mo) may be included. Preferably, a lower limit of a content of molybdenum (Mo) may be 0.11%, and more preferably, the lower limit of the content of molybdenum (Mo) may be 0.12%.
- an upper limit of the content of molybdenum (Mo) may be limited to 0.5%.
- the upper limit of the content of molybdenum (Mo) may be 0.48%, and more preferably, the upper limit of the content of molybdenum (Mo) may be 0.45%.
- Niobium (Nb) is an element which is effective for increasing hardenability of austenite by being dissolved in austenite, and increasing strength of steel and suppressing growth of austenite crystal grains by forming carbonitrides such as Nb(C,N).
- 0.01% or more of niobium (Ni) may be included.
- an upper limit of a content of niobium (Nb) may be limited to 0.05%.
- the upper limit of the content of niobium (Nb) content may be 0.04%, and more preferably, the upper limit of the content of niobium (Nb) may be 0.03%.
- Boron (B) is an element effectively contributing to strength improvement by increasing quenching properties of steel even with a small addition amount thereof.
- 0.0002% or more of boron (B) may be contained.
- a lower limit of a content of boron (B) may be 0.0005%, and more preferably, the lower limit of the content of boron (B) may be 0.001%.
- an upper limit of the content of boron (B) may be limited to 0.005%.
- the upper limit of the content of boron (B) may be 0.004%, and more preferably, the upper limit of the content of boron (B) may be 0.003%.
- Ca an element having a good binding force with sulfur (S) and producing CaS on the periphery (around) MnS, thereby suppressing elongation of MnS to improve toughness in a direction perpendicular to a rolling direction.
- CaS produced by adding Ca has an effect of increasing corrosion resistance under a humid external environment.
- 0.0005% or more of Ca may be included.
- a lower limit of a content of calcium (Ca) may be 0.001%.
- an upper limit of the content of calcium (Ca) may be limited to 0.004%.
- the upper limit of the content of calcium (Ca) may be 0.003%.
- bullet-proof steel of the present disclosure may further include the following elements for the purpose of favorably securing target physical properties.
- the bullet-proof steel of the present disclosure may further include at least one of titanium (Ti) and vanadium (V).
- Titanium (Ti) is an element which maximizes the effect of boron (B), which is an element favorable to improve quenching properties of steel. That is, titanium (Ti) is bonded to nitrogen (N) in steel to be precipitated into TiN to reduce the content of solid-solubilized N, while suppressing formation of BN of B therefrom to increase solid-solubilized B, thereby maximizing improvement of quenching properties. In order to sufficiently obtain the effect described above, 0.005% or more of titanium (Ti) may be contained. However, when titanium (Ti) is excessively added, coarse TiN precipitates may be formed and toughness of steel may be deteriorated, so in the present disclosure, an upper limit of the content of titanium (Ti) may be limited to 0.025%.
- V Vanadium (V): 0.2% or less (including 0%)
- Vanadium (V) is an element favorable to form a VC carbide when reheating after hot rolling, thereby suppressing growth of austenite crystal grains and improving quenching properties of steel to secure strength and toughness.
- vanadium (V) is a relatively expensive element, an upper limit of a content of vanadium (V) may be limited to 0.2% in consideration of manufacturing costs.
- the bullet-proof steel according to an aspect of the present disclosure may include a remainder of Fe and other inevitable impurities in addition to the components described above.
- the component since in the common manufacturing process, unintended impurities may be inevitably incorporated from raw materials or the surrounding environment, the component may not be excluded. Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification. In addition, further addition of effective ingredients other than the above-mentioned ingredients is not entirely excluded.
- the bullet-proof steel according to an aspect of the present disclosure may satisfy the following [Relational Expression 1]. 10 * C * Si ⁇ 2.5
- [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel sheet, and 0 is substituted if the corresponding element is not intentionally added.
- the inventors of the present disclosure have conducted in-depth research on a method capable of securing high-hardness characteristics and excellent low-temperature impact toughness of a steel sheet at the same time, and have derived that it is effective to control not only a content range of each respective alloy composition, but also a relative content range of the specific alloy composition included in the steel sheet.
- not only the content range of each respective alloy composition included in the steel sheet is controlled to be within a certain range, but also the relative content range of carbon (C) and silicon (Si) is controlled to be within a certain range, as illustrated in [Relational Expression 1], so that high hard characteristics and excellent low-temperature impact toughness may be effectively compatible.
- 10*[C]*[Si] defined by the Relational Expression 1 may be 2.9 or more.
- the bullet-proof steel of the present disclosure having the alloy composition described above may have a tempered martensite base structure including retained austenite as a microstructure, and may further include other inevitable structures.
- a fraction of retained austenite may be 1% by area to 10% by area, and a fraction of tempered martensite may be 90% or more by area.
- Retained austenite is a structure remaining without being completely phase transformed into martensite during a rapid cooling heat treatment, and has relatively low hardness but excellent toughness as compared to martensite.
- the bullet-proof steel of the present disclosure may include 1% or more by area of retained austenite, more preferably 2% or more by area of retained austenite.
- an upper limit of the fraction of the retained austenite may be set to be 10% by area.
- the upper limit of the fraction of the retained austenite may be 5% by area, and a lower limit of the fraction of the tempered martensite may be 95°; by area.
- the bullet-proof steel of the present disclosure may have the above-described microstructural configuration over the entire thickness.
- the bullet-proof steel of the present disclosure having the above-described alloy composition and the proposed microstructure may have a thickness of 6 to 40 mm and a surface hardness of the bullet-proof steel may be 360 to 440HB, exhibiting ultra-high hardness, and may have an impact absorption energy of 27 J or more at -40 °C, exhibiting excellent low-temperature toughness.
- the surface hardness refers to an average value of three measurements after milling a surface of the armor steel at 2 mm in a thickness direction using a Brinell hardness tester (load: 3000 kgf, 10 mm tungsten injection port).
- a steel slab having a predetermined component is prepared. Since the steel slab of the present disclosure has an alloy composition corresponding to the alloy composition of the hot-rolled steel sheet described above (including [Relational Expression 1]), a description of the alloy composition of the steel slab is substituted for the description of the alloy composition of the above-described hot-rolled steel sheet.
- the bullet-proof steel may be manufactured by preparing a steel slab satisfying the alloy composition described above, and then subjecting the steel slab to the processes of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)].
- the processes of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)] will be described in detail.
- a steel slab having the alloy composition proposed in the present disclosure is prepared, which may be then heated in a temperature range of 1050 to 1250°C.
- the steel slab may be heated in a temperature range of 1050 to 1250°C.
- the steel slab heated as described above may be rolled, and then may be subjected to rough rolling and finish hot rolling to manufacture a hot-rolled steel sheet.
- the heated steel slab is roughly rolled in a temperature range of 950 to 1150°C to be manufactured into a bar, which may be then subjected to finish hot rolling in a temperature range of 850 to 950°C.
- the hot-rolled steel sheet manufactured through the rolling process described above is air cooled to room temperature, and then heated to a residence time of 1.3t + 10 minutes (t: plate thickness (mm)) or more in a temperature range of 880 to 930°C.
- the heating is performed for reverse transformation of a hot-rolled steel sheet composed of ferrite and pearlite into an austenite single phase.
- a heating temperature is lower than 880°C, austenitization is not sufficiently achieved, and coarse soft ferrite is mixed, and thus hardness of a final product may be lowered.
- the temperature thereof is higher than 930°C, there is an effect of increasing quenching properties due to coarse austenite crystal grains, but there is a disadvantage in terms of thermal efficiency during mass production. Therefore, heating during a primary heat treatment is preferably performed in a range of 880 to 930°C.
- a lower limit of the heating temperature is more preferably 885 °C, even more preferably 890°C, and most preferably 895°C.
- an upper limit of the heating temperature is more preferably 925 °C, even more preferably 920 °C, and most preferably 915 °C.
- the residence time during the heating is preferably 1.3t + 10 minutes (t: plate thickness (mm)) or more.
- the residence time during the heating is more preferably 1.3t + 12 minutes (t: plate thickness (mm)) or more, even more preferably 1.3t + 13 minutes (t: plate thickness (mm)) or more, and most preferably 1.5t + 15 minutes (t: plate thickness (mm)) or more.
- an upper limit of the residence time during the primary heat treatment is not particularly limited.
- the residence time during the heating exceeds 1.3 t + 60 minutes (t: plate thickness (mm))
- austenite crystal grains become coarse, so that quenching properties may increase, but there may be a disadvantage in that productivity is relatively lowered. Therefore, the residence time during the heating is preferably 1.3t + 60 minutes (t: plate thickness (mm)) or less.
- the residence time during the heating is more preferably 1.3t + 50 minutes (t: plate thickness (mm)) or less, even more preferably 1.3t + 40 minutes (t: plate thickness (mm)) or less, and most preferably 1.3t + 30 minutes (t: plate thickness (mm)) or less.
- the heated hot-rolled steel sheet may be cooled to 120 °C or lower at a cooling rate of 10°C/s or more with respect to a plate thickness center portion(e.g., 1/2t point, t: plate thickness (mm)).
- the cooling is preferably rapid cooling through water cooling.
- the cooling rate is less than 10°C/s or a cooling end temperature is higher than 120 °C, there is a concern that a ferrite phase may be formed or a bainite phase may be excessively formed during cooling. Therefore, the cooling is preferably performed to 120 °C or lower at a cooling rate of 10°C/s or more. The faster the cooling rate, the more favorable it is to form the microstructure to be obtained in the present disclosure.
- an upper limit of the cooling rate is not particularly limited, and it may be appropriately set in consideration of facility limitations by any person skilled in the art.
- the cooling end temperature is more preferably 100°C or lower, even more preferably 80°C or lower, and most preferably 50°C or lower.
- the hot-rolled steel sheet manufactured through the above-described primary heat treatment may be heated to a temperature range of 350 °C or lower and maintained for 1.9t+10 minutes (t: plate thickness (mm)) or more.
- the reheating is performed to release internal stress of a hot-rolled steel sheet fully composed of martensite after quenching.
- a tempering heat treatment As dislocation density inside a material thereof decreases through such a tempering heat treatment, hardness may decrease somewhat, but toughness may be secured.
- a subsequent tempering heat treatment is essential if no special element is added.
- a tempering temperature is higher than 350 °C, the dislocation density inside the martensite is excessively reduced, and thus hardness of a final product may be lowered.
- a lower limit of the tempering temperature is not separately specified, but is preferably 100 °C or higher in order to obtain the effect described above. It is preferable to perform tempering, more preferably at a temperature of 125 °C or higher, and even more preferably 150 °C or higher.
- a lower limit of a holding time during the tempering is not particularly limited.
- the holding time during the tempering is less than 1.9t + 10 minutes (t: plate thickness (mm))
- a thickness center portion compared to the surface thereof may not be sufficiently heated, as the heat treatment is performed at a relatively low temperature for a short time. Therefore, the holding time during the tempering is preferably 1.9t + 10 minutes (t: plate thickness (mm)) or more.
- the holding time during the tempering is more preferably 1.9t + 12 minutes (t: plate thickness (mm)) or more, more preferably 1.9t + 15 minutes (t: plate thickness (mm)) or less, and most preferably 1.9t + 20 minutes (t: plate thickness (mm)) or more.
- the hot-rolled steel sheet according to an aspect of the present disclosure may have softened tempered martensite as a base structure.
- the hot-rolled steel sheet obtained through the above-described series of manufacturing processes is a steel material having a thickness of 6 to 40 mm, and can provide excellent bullet-proof resistance by securing high hardness and high toughness.
- Specimen 11 in Table 2 refers to a specimen that was not subjected to the second heat treatment (tempering) after the first heat treatment (quenching).
- Table 1 St ee 1 ty pe Alloy composition(weight %) Relation al Expressi on 1 C Si Mn P* S* Ni Cr Mo Nb V Al Ca* Ti B* N* A 0.3 6 1.3 7 1.4 5 76 19 1.1 3 0.6 8 0.2 8 0.0 3 - 0.0 4 16 0.01 2 21 45 4.93 B 0.1 6 0.2 9 1.0 8 72 20 0.4 2 0.4 6 0.1 3 0.0 1 0.0 2 0.0 3 18 0.01 7 23 48 0.46 C 0.2 4 1.3 9 1.1 2 73 18 0.9 6 0.5 5 0.3 9 0.0 2 - 0.0 3 22 - 21 44 3.34 D 0.2 0 1.6 5 1.2 76 19 1.1 4 0.8 1 0.4 4 0.0 3 0.0 4 0.0 3 21 - 19 46 3.30 E 0.2 3 1.2 6 0.9 6 77 17
- Cooli ng end tempe ratur e (°C) Coolin g rate (°C/s) Heating tempera ture (°C) Holdin g time (min.) 1 A 10 1147 1055 861 909 36 30 65.2 208 39 2 A 25 1149 1029 928 913 54 37 45.9 227 60 3 A 50 1155 1044 910 904 85 23 12.5 212 95 4 B 15 1162 1025 899 907 43 24 44.1 301 39 5 B 30 1148 1035 923 905 60 32 31.9 254 75 6 B 60 1153 980 915 904 89 43 7.6 203 114 7 C 8 1185 1059 886 913 32 19 62.2 215 36 8 C 25 1129 1033 925 916 54 25 43.3 391 60 9 C 50 1131 965 911 907 86 21 9.4 224 116 10 D 12 1145 1046 924 905 40 18 50.5 209 45 11 D 25 1138 1030 922 914 55 19 40.7 - - 12 D 40 1149
- microstructure of each hot-rolled steel sheet was cut into an arbitrary size as a specimen to manufacture a mirror surface, a Nital etching solution was used to corrode the specimen, and then an optical microscope and a scanning electron microscope (SEM) were used to observe a 1/2t point which was a thickness center part. In this case, a fraction of the microstructure was measured by electron back-scattered diffraction (EBSD) analysis.
- EBSD electron back-scattered diffraction
- hardness and toughness of each hot-rolled steel sheet were measured using a Brinell hardness tester (load: 3000 kgf, 10 mm tungsten injection port) and a Charpy impact tester, respectively.
- a Brinell hardness tester load: 3000 kgf, 10 mm tungsten injection port
- a Charpy impact tester a specimen was collected at 1/4t point in the thickness direction, and then an average value of three measurements at -40°C was used.
- specimens satisfying the alloy composition and process conditions of the present disclosure have a surface harness of 360 to 440 HB and an impact absorption energy of 27 J or more at -40°C, but specimens not satisfying at least one of the alloy compositions or process conditions of the present disclosure do not have a surface hardness of 360 to 440 HB or an impact absorption energy of 27 J or more at -40°C at the same time.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention can provide a bullet-proof steel capable of providing excellent bullet-proof properties by having high hardness characteristics and excellent low-temperature impact toughness, and a method for manufacturing same.
Description
- The present disclosure relates to a material appropriate for armored vehicles, explosion-proof structures, and the like, and more particularly to bullet-proof steel having excellent low-temperature impact toughness and having high hardness, and a method for manufacturing the same.
- Bullet-proof steel is a material of which a surface is made very hard for its main function of blocking bullets, and is used where protection is required, such as for an exterior of armored vehicles used on the battlefield. Since bulletproof performance is directly related to human life, research to improve the performance of bulletproof materials has been actively conducted in the past, and recently, a non-ferrous material such as titanium and aluminum has been developed.
- The non-ferrous material has an advantage of weight reduction compared to a steel material, but is relatively expensive and has poor workability. As compared to the non-ferrous material, since the steel material is relatively inexpensive and may change physical properties such as harness relatively easily, the steel material is widely used as a material for self-propelled artillery, wheeled armored vehicles, and the like.
- Hardness is one of the most important physical properties for securing the performance of bullet-proof steel, but simple high hardness does not guarantee bulletproof performance. A high hardness characteristic is a factor that increases resistance to bullets penetrating through a material, but the material having high hardness may be relatively easily broken, so the high hardness characteristic cannot necessarily guarantee excellent bulletproof performance. Therefore, there is a need to develop a material that can simultaneously secure brittle fracture resistance to external impact as well as high hardness characteristics rather than simply promoting high hardness of the material.
- (Patent Document)
Korean Patent Publication No. 10-2018-0043788 (published on April 30, 2018 - An aspect of the present disclosure is to provide bullet-proof steel having high hardness characteristics and excellent low-temperature impact toughness and a method for manufacturing the same.
- An object of the present disclosure is not limited to the above description. The object of the present disclosure will be understood from the entire content of the present specification, and a person skilled in the art to which the present disclosure pertains will understand an additional object of the present disclosure without difficulty.
- According to an aspect of the present disclosure, a high- hardness bullet-proof steel having excellent low-temperature impact toughness includes, by weight: 0.18 to 0.25% of carbon (C), 1.0 to 2.0% of silicon (Si), 0.5 to 1.6% of manganese (Mn), 0.5 to 1.2% of nickel (Ni), 0.4 to 1.5% of chromium (Cr), 0.05% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.006% or less of nitrogen (N), 0.07% or less of aluminum (Al) (excluding 0%), 0.1 to 0.5% of molybdenum (Mo), 0.01 to 0.05% of niobium (Nb), 0.0002 to 0.005% of boron (B), 0.0005 to 0.004% of calcium (Ca), with a balance of iron (Fe) and inevitable impurities, satisfying the following [Relational Expression 1], wherein a tempered martensite base structure including retained austenite is included as a microstructure.
- In Relational Expression 1, [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel sheet, and 0 is substituted when the corresponding element is not intentionally added.
- The bullet-proof steel may further include, by weight: at least one of 0.005 to 0.025% of titanium (Ti) and 0.2% or less of vanadium (V).
- A fraction of the tempered martensite may be 90% or more by area, and a fraction of the retained austenite may be 0.5% by area to 5% by area.
- The bullet-proof steel may have a surface hardness of 360 to 440 HB, and an impact absorption energy of 27 J or more at -40°C.
- The bullet-proof steel may have a thickness of 5 to 20 mm.
- According to an aspect of the present disclosure, a manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness includes operations of: preparing a steel slab including, by weight: 0.18 to 0.25% of carbon (C), 1.0 to 2.0% of silicon (Si), 0.5 to 1.6% of manganese (Mn), 0.5 to 1.2% of nickel (Ni), 0.4 to 1.5% of chromium (Cr), 0.05% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.006% or less of nitrogen (N), 0.07% or less of aluminum (Al) (excluding 0%), 0.1 to 0.5% of molybdenum (Mo), 0.01 to 0.05% of niobium (Nb), 0.0002 to 0.005% of boron (B), 0.0005 to 0.004% of calcium (Ca), with a balance of iron (Fe) and inevitable impurities, satisfying the following [Relational Expression 1]; heating the steel slab in a temperature range of 1050 to 1250 °C; rough rolling the heated steel slab in a temperature range of 950 to 1150 °C; subjecting the heated steel slab to finish hot rolling in a temperature range of 850 to 950 °C after the rough rolling to manufacture a hot-rolled steel sheet; performing a primary heat-treatment of heating the hot-rolled steel sheet to a temperature range of 880 to 930 °C and then cooling the same to a cooling end temperature of 150 °C or lower at a cooling rate of 10 °C/s or more; and performing a secondary heat-treatment of heating the primarily heat-treated hot-rolled steel sheet to a temperature range of 350 °C or lower and maintaining the same.
- In Relational Expression 1, [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel slab, and 0 is substituted when the corresponding element is not intentionally added.
- The steel slab may further include, by weight: at least one of 0.005 to 0.025% of titanium (Ti) and 0.2% or less of vanadium (V).
- A residence time during the first heat treatment may be 1.3t * 10 minutes (t: plate thickness (mm)) or more.
- A holding time during the secondary heat treatment may be 1.9t+10 minutes (t: plate thickness (mm)) or more.
- The solution to the above problems does not enumerate all the features of the present disclosure, and various beneficial merits of the present disclosure are not limited to the descriptions above, and may be more easily understood in a process of describing specific exemplary embodiments in the present disclosure.
- As set forth above, according to the present disclosure, bullet-proof steel having excellent low-temperature toughness while having ultra-high hardness may be provided.
- The present disclosure may provide bullet-proof steel having a target level of physical properties without performing a further heat treatment from optimization of alloy compositions and manufacturing conditions, and thus, is economically favorable.
- The effect of the present disclosure is not limited to the above, and may be interpreted as including an effect that can be inferred from the description described below by those skilled in the art.
- The present disclosure relates to a high-hardness bullet-proof steel having excellent low-temperature impact toughness and a method for manufacturing the same . Hereinafter, preferred embodiments of the present disclosure will be described. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to the embodiments described below. The present embodiments are provided to those skilled in the art to further elaborate the present disclosure.
- The present inventors have studied in depth, in order to provide a steel material having excellent physical properties such as high hardness characteristics, low-temperature impact toughness, and the like, which are essentially required physical properties, as a material which may be appropriately applied to tracked armored vehicles, explosion-proof structures, and the like.
- In particular, the bulletproof performance of the steel material was intended to be improved by an economically favorable method, and thus, the present disclosure was provided.
- Hereinafter, bullet-proof steel according to an aspect of the present disclosure will be described in more detail.
- Hereinafter, a steel composition of the present disclosure will be described in more detail. Hereinafter, % represents a content of each element based on weight, unless otherwise particularly specified.
- Carbon (C) is an element which is effective for improving strength and hardness in steel having a low-temperature transformation phase such as a martensite or bainite phase, and is effective for improving hardenability. In order to sufficiently obtain the effect described above, 0.18% or more of carbon (C) may be included. Preferably, a lower limit of a content of carbon (C) may be 0.19%, and more preferably, the lower limit of the content of carbon (C) may be 0.20%. However, when carbon (C) is excessively added, there may be a concern that weldability and toughness of steel are deteriorated, so in the present disclosure, an upper limit of the content of carbon (C) may be limited to 0.25%. Preferably, the upper limit of the content of carbon (C) may be 0.24%.
- Silicon (Si) is an element which is effective for improving strength due to solid solution strengthening together with a deoxidation effect, and is also an element suppressing formation of carbides such as cementite in a steel material containing a certain amount or more of C to promote production of residual austenite. In particular, since residual austenite which is uniformly distributed in steel having a low-temperature transformation phase such as martensite and bainite may effectively contribute to improvement of impact toughness without strength reduction. Therefore, in order to sufficiently obtain the effect described above, in the present disclosure, 1.0% or more of silicon (Si) may be included. Preferably, a lower limit of a content of silicon (Si) may be 1.1%, and more preferably, the lower limit of the content of silicon (Si) may be 1.2%. However, when silicon (Si) is excessively added, weldability may be rapidly deteriorated, so in the present disclosure, an upper limit of the content of silicon (Si) may be limited to 2.0%. Preferably, the upper limit of the content of silicon (Si) may be 1.9%, and more preferably, the upper limit of the content of silicon (Si) may be 1.8%.
- Manganese (Mn) is an element favorable to suppress production of ferrite and lower an Ar3 temperature, thereby improving quenching properties of steel to increase strength and toughness. In order to obtain a target level of hardness in the present disclosure, 0.5% or more of manganese (Mn) may be included. Preferably, a lower limit of a content of manganese (Mn) may be 0.6%, and more preferably, the lower limit of the content of manganese (Mn) may be 0.7%. However, when manganese (Mn) is excessively added, there may be a concern that weldability is deteriorated and center segregation is encouraged to deteriorate the physical properties in the center part of steel, so in the present disclosure, an upper limit of the content of manganese (Mn) may be limited to 1.6%. Preferably, the upper limit of the content of manganese (Mn) may be 1.5%, and more preferably, the upper limit of the content of manganese (Mn) may be 1.45%.
- Nickel (Ni) is an element favorable to improve both strength and toughness of steel. In order to obtain the effect described above, in the present disclosure, 0.5% or more of nickel (Ni) may be included. Preferably, a lower limit of a content of nickel (Ni) may be 0.6%, and more preferably, the lower limit of the content of nickel (Ni) may be 0.7%. However, nickel (Ni) is an expensive element, when nickel (Ni) is excessively added, manufacturing costs may be greatly increased, so in the present disclosure, an upper limit of the content of nickel (Ni) may be limited to 1.2%. Preferably, the upper limit of the content of nickel (Ni) may be 1.17%, and more preferably, the upper limit of the content of nickel (Ni) may be 1.15%.
- Chromium (Cr) is an element of increasing quenching properties of steel to improve strength, and effectively contributing to securing hardness in a surface part and a center part of steel. In addition, since chromium (Cr) is a relatively inexpensive element, chromium (Cr) is also an element for economically securing hardness and toughness. In order to obtain the effect described above, in the present disclosure, 0.4% or more of chromium (Cr) may be included. Preferably, a lower limit of a content of chromium (Cr) may be 0.45%. However, when chromium (Cr) is excessively added, weldability may be deteriorated, so in the present disclosure, an upper limit of the content of chromium (Cr) may be limited to 1.5%. Preferably, the upper limit of the content of chromium (Cr) may be 1.4%, and more preferably, the upper limit of the content of chromium (Cr) may be 1.3%.
- Phosphorus (P) is an element which is inevitably contained in steel, and is also an element which deteriorates toughness of the steel. Thus, it is preferred to lower a content of P as much as possible. In the present disclosure, even in the case of including phosphorus (P) up to 0.05%, the physical properties of the steel are not significantly influenced, and thus, an upper limit of the content of phosphorus (P) may be limited to 0.05%. More favorably, the content thereof may be limited to 0.03% or less. However, 0% may be excluded considering an inevitably contained level.
- Sulfur (S) is an element which is inevitably contained in steel, and is also an element forming MnS inclusions to deteriorate toughness of steel. Thus, it is preferred to lower a content of S as much as possible. In the present disclosure, even in the case of including sulfur (S) up to 0.02%, the physical properties of the steel are not significantly influenced, and thus, an upper limit of the content of sulfur (S) may be limited to 0.02%. More favorably, the content thereof may be limited to 0.01% or less. However, 0% may be excluded considering an inevitably contained level.
- Nitrogen (N)is an element which is favorable to improve strength of steel by forming precipitates in steel, but when a content of nitrogen (N) is more than a certain level, which may rather cause deterioration in toughness of steel. In the present disclosure, there is no difficulty in securing strength even when N is not contained, so in the present disclosure, an upper limit of a content of nitrogen (N) may be limited to 0.006%. However, 0% may be excluded considering an inevitably contained level.
- Aluminum (Al) is an element effective for lowering an oxygen content in molten steel as a deoxidizing agent of steel. However, when aluminum (Al) is excessively added, cleanliness of steel may be impaired, so in the present disclosure, an upper limit of a content of aluminum (Al) may be limited to 0.07%.
- On the other hand, when the content of aluminum (Al) is excessively lowered, a load may occur in a steelmaking process and manufacturing costs may be increased, and thus, in the present disclosure, 0% may be excluded from a lower limit of the content of aluminum (Al), and the lower limit thereof may be 0.01%.
- Molybdenum (Mo) is an element favorable to increase quenching properties of steel, and in particular, to improve hardness of a thick material having a certain thickness or more. In order to obtain the effect described above, in the present disclosure, 0.1% or more of molybdenum (Mo) may be included. Preferably, a lower limit of a content of molybdenum (Mo) may be 0.11%, and more preferably, the lower limit of the content of molybdenum (Mo) may be 0.12%. However, when molybdenum (Mo) is excessively added, not only manufacturing costs may be increased, but also weldability may be deteriorated, so in the present disclosure, an upper limit of the content of molybdenum (Mo) may be limited to 0.5%. Preferably, the upper limit of the content of molybdenum (Mo) may be 0.48%, and more preferably, the upper limit of the content of molybdenum (Mo) may be 0.45%.
- Niobium (Nb) is an element which is effective for increasing hardenability of austenite by being dissolved in austenite, and increasing strength of steel and suppressing growth of austenite crystal grains by forming carbonitrides such as Nb(C,N). In order to sufficiently obtain the effect described above, in the present disclosure, 0.01% or more of niobium (Ni) may be included. However, when niobium (Ni) is excessively added, coarse precipitates may be formed to become a starting point of brittle fracture, so in the present disclosure, an upper limit of a content of niobium (Nb) may be limited to 0.05%. Preferably, the upper limit of the content of niobium (Nb) content may be 0.04%, and more preferably, the upper limit of the content of niobium (Nb) may be 0.03%.
- Boron (B) is an element effectively contributing to strength improvement by increasing quenching properties of steel even with a small addition amount thereof. In order to sufficiently obtain the effect, in the present disclosure, 0.0002% or more of boron (B) may be contained. Preferably, a lower limit of a content of boron (B) may be 0.0005%, and more preferably, the lower limit of the content of boron (B) may be 0.001%. However, when boron (B) is excessively added, toughness and weldability of steel may be rather deteriorated, so in the present disclosure, an upper limit of the content of boron (B) may be limited to 0.005%. Preferably, the upper limit of the content of boron (B) may be 0.004%, and more preferably, the upper limit of the content of boron (B) may be 0.003%.
- Calcium (Ca) an element having a good binding force with sulfur (S) and producing CaS on the periphery (around) MnS, thereby suppressing elongation of MnS to improve toughness in a direction perpendicular to a rolling direction. In addition, CaS produced by adding Ca has an effect of increasing corrosion resistance under a humid external environment. In order to sufficiently obtain the effect described above, 0.0005% or more of Ca may be included. Preferably, a lower limit of a content of calcium (Ca) may be 0.001%. However, when calcium (Ca) is excessively added, defects such as nozzle clogging, or the like, may be caused in a steelmaking operation, so in the present disclosure, an upper limit of the content of calcium (Ca) may be limited to 0.004%. Preferably, the upper limit of the content of calcium (Ca) may be 0.003%.
- In addition to the above-described alloy composition, bullet-proof steel of the present disclosure may further include the following elements for the purpose of favorably securing target physical properties.
- Specifically, the bullet-proof steel of the present disclosure may further include at least one of titanium (Ti) and vanadium (V).
- Titanium (Ti) is an element which maximizes the effect of boron (B), which is an element favorable to improve quenching properties of steel. That is, titanium (Ti) is bonded to nitrogen (N) in steel to be precipitated into TiN to reduce the content of solid-solubilized N, while suppressing formation of BN of B therefrom to increase solid-solubilized B, thereby maximizing improvement of quenching properties. In order to sufficiently obtain the effect described above, 0.005% or more of titanium (Ti) may be contained. However, when titanium (Ti) is excessively added, coarse TiN precipitates may be formed and toughness of steel may be deteriorated, so in the present disclosure, an upper limit of the content of titanium (Ti) may be limited to 0.025%.
- Vanadium (V) is an element favorable to form a VC carbide when reheating after hot rolling, thereby suppressing growth of austenite crystal grains and improving quenching properties of steel to secure strength and toughness. However, since vanadium (V) is a relatively expensive element, an upper limit of a content of vanadium (V) may be limited to 0.2% in consideration of manufacturing costs.
- The bullet-proof steel according to an aspect of the present disclosure may include a remainder of Fe and other inevitable impurities in addition to the components described above. However, since in the common manufacturing process, unintended impurities may be inevitably incorporated from raw materials or the surrounding environment, the component may not be excluded. Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification. In addition, further addition of effective ingredients other than the above-mentioned ingredients is not entirely excluded.
-
- In Relational Expression 1, [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel sheet, and 0 is substituted if the corresponding element is not intentionally added.
- The inventors of the present disclosure have conducted in-depth research on a method capable of securing high-hardness characteristics and excellent low-temperature impact toughness of a steel sheet at the same time, and have derived that it is effective to control not only a content range of each respective alloy composition, but also a relative content range of the specific alloy composition included in the steel sheet. In the present disclosure, not only the content range of each respective alloy composition included in the steel sheet is controlled to be within a certain range, but also the relative content range of carbon (C) and silicon (Si) is controlled to be within a certain range, as illustrated in [Relational Expression 1], so that high hard characteristics and excellent low-temperature impact toughness may be effectively compatible. 10*[C]*[Si] defined by the Relational Expression 1 may be 2.9 or more.
- The bullet-proof steel of the present disclosure having the alloy composition described above may have a tempered martensite base structure including retained austenite as a microstructure, and may further include other inevitable structures. In this case, preferably, a fraction of retained austenite may be 1% by area to 10% by area, and a fraction of tempered martensite may be 90% or more by area.
- Retained austenite is a structure remaining without being completely phase transformed into martensite during a rapid cooling heat treatment, and has relatively low hardness but excellent toughness as compared to martensite. For this effect, the bullet-proof steel of the present disclosure may include 1% or more by area of retained austenite, more preferably 2% or more by area of retained austenite. On the other hand, when the retained austenite is excessively formed, the low-temperature impact toughness greatly increases, but it is difficult to secure target hardness characteristics. Therefore, in the present disclosure, an upper limit of the fraction of the retained austenite may be set to be 10% by area. The upper limit of the fraction of the retained austenite may be 5% by area, and a lower limit of the fraction of the tempered martensite may be 95°; by area.
- Meanwhile, the bullet-proof steel of the present disclosure may have the above-described microstructural configuration over the entire thickness.
- The bullet-proof steel of the present disclosure having the above-described alloy composition and the proposed microstructure may have a thickness of 6 to 40 mm and a surface hardness of the bullet-proof steel may be 360 to 440HB, exhibiting ultra-high hardness, and may have an impact absorption energy of 27 J or more at -40 °C, exhibiting excellent low-temperature toughness.
- Here, the surface hardness refers to an average value of three measurements after milling a surface of the armor steel at 2 mm in a thickness direction using a Brinell hardness tester (load: 3000 kgf, 10 mm tungsten injection port).
- Hereinafter, a method for manufacturing bullet-proof steel according to an aspect of the present disclosure will be described in more detail.
- A steel slab having a predetermined component is prepared. Since the steel slab of the present disclosure has an alloy composition corresponding to the alloy composition of the hot-rolled steel sheet described above (including [Relational Expression 1]), a description of the alloy composition of the steel slab is substituted for the description of the alloy composition of the above-described hot-rolled steel sheet.
- In brief, the bullet-proof steel may be manufactured by preparing a steel slab satisfying the alloy composition described above, and then subjecting the steel slab to the processes of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)]. Hereinafter, each process condition will be described in detail.
- First, a steel slab having the alloy composition proposed in the present disclosure is prepared, which may be then heated in a temperature range of 1050 to 1250°C.
- When the temperature is lower than 1050°C during the heating, deformation resistance of steel is increased, so that a subsequent rolling process may not be effectively performed. On the other hand, when the temperature is higher than 1250°C, austenite crystal grains are coarsened, so that non-uniform structure may be formed.
- Therefore, the steel slab may be heated in a temperature range of 1050 to 1250°C.
- The steel slab heated as described above may be rolled, and then may be subjected to rough rolling and finish hot rolling to manufacture a hot-rolled steel sheet.
- First, the heated steel slab is roughly rolled in a temperature range of 950 to 1150°C to be manufactured into a bar, which may be then subjected to finish hot rolling in a temperature range of 850 to 950°C.
- When the temperature is lower than 950°C during the rough rolling, a rolling load is increased to reduce the steel slab relatively weakly, and thus, deformation is not sufficiently transferred to a center of the slab in the thickness direction, and as a result, defects such as voids may not be removed. On the other hand, when the temperature thereof is higher than 1150°C, recrystallization granularity is coarsened, which may be harmful to toughness.
- When the temperature is lower than 850°C during the finish hot rolling, two-phase region rolling is performed, so that there is a concern that ferrite may be produced in the microstructure. On the other hand, when the temperature thereof is higher than 950°C, the granularity of the final structure is coarsened to deteriorate low-temperature toughness.
- The hot-rolled steel sheet manufactured through the rolling process described above is air cooled to room temperature, and then heated to a residence time of 1.3t + 10 minutes (t: plate thickness (mm)) or more in a temperature range of 880 to 930°C.
- The heating is performed for reverse transformation of a hot-rolled steel sheet composed of ferrite and pearlite into an austenite single phase. When a heating temperature is lower than 880°C, austenitization is not sufficiently achieved, and coarse soft ferrite is mixed, and thus hardness of a final product may be lowered. On the other hand, when the temperature thereof is higher than 930°C, there is an effect of increasing quenching properties due to coarse austenite crystal grains, but there is a disadvantage in terms of thermal efficiency during mass production. Therefore, heating during a primary heat treatment is preferably performed in a range of 880 to 930°C. A lower limit of the heating temperature is more preferably 885 °C, even more preferably 890°C, and most preferably 895°C. In addition, an upper limit of the heating temperature is more preferably 925 °C, even more preferably 920 °C, and most preferably 915 °C.
- Meanwhile, when a residence time during the primary heat treatment is less than 1.3t + 10 minutes (t: plate thickness (mm)), austenitization does not sufficiently occur, so that phase transformation by subsequent rapid cooling, that is, a martensitic structure cannot be sufficiently obtained. Therefore, the residence time during the heating is preferably 1.3t + 10 minutes (t: plate thickness (mm)) or more. The residence time during the heating is more preferably 1.3t + 12 minutes (t: plate thickness (mm)) or more, even more preferably 1.3t + 13 minutes (t: plate thickness (mm)) or more, and most preferably 1.5t + 15 minutes (t: plate thickness (mm)) or more.
- In the present disclosure, an upper limit of the residence time during the primary heat treatment is not particularly limited. However, when the residence time during the heating exceeds 1.3 t + 60 minutes (t: plate thickness (mm)), austenite crystal grains become coarse, so that quenching properties may increase, but there may be a disadvantage in that productivity is relatively lowered. Therefore, the residence time during the heating is preferably 1.3t + 60 minutes (t: plate thickness (mm)) or less. The residence time during the heating is more preferably 1.3t + 50 minutes (t: plate thickness (mm)) or less, even more preferably 1.3t + 40 minutes (t: plate thickness (mm)) or less, and most preferably 1.3t + 30 minutes (t: plate thickness (mm)) or less.
- Thereafter, the heated hot-rolled steel sheet may be cooled to 120 °C or lower at a cooling rate of 10°C/s or more with respect to a plate thickness center portion(e.g., 1/2t point, t: plate thickness (mm)). In this case, the cooling is preferably rapid cooling through water cooling. When the cooling rate is less than 10°C/s or a cooling end temperature is higher than 120 °C, there is a concern that a ferrite phase may be formed or a bainite phase may be excessively formed during cooling. Therefore, the cooling is preferably performed to 120 °C or lower at a cooling rate of 10°C/s or more. The faster the cooling rate, the more favorable it is to form the microstructure to be obtained in the present disclosure. Meanwhile, in the present disclosure, an upper limit of the cooling rate is not particularly limited, and it may be appropriately set in consideration of facility limitations by any person skilled in the art. The cooling end temperature is more preferably 100°C or lower, even more preferably 80°C or lower, and most preferably 50°C or lower.
- The hot-rolled steel sheet manufactured through the above-described primary heat treatment may be heated to a temperature range of 350 °C or lower and maintained for 1.9t+10 minutes (t: plate thickness (mm)) or more.
- The reheating is performed to release internal stress of a hot-rolled steel sheet fully composed of martensite after quenching. As dislocation density inside a material thereof decreases through such a tempering heat treatment, hardness may decrease somewhat, but toughness may be secured. In the case of bullet-proof steel, since it is necessary not only to have high hardness but also to have excellent low-temperature impact toughness, such a subsequent tempering heat treatment is essential if no special element is added. When a tempering temperature is higher than 350 °C, the dislocation density inside the martensite is excessively reduced, and thus hardness of a final product may be lowered. On the other hand, when the tempering temperature is too low, the decrease in hardness can be prevented, but the dislocation density becomes too high, which is disadvantageous in terms of securing impact toughness. In the present disclosure, a lower limit of the tempering temperature is not separately specified, but is preferably 100 °C or higher in order to obtain the effect described above. It is preferable to perform tempering, more preferably at a temperature of 125 °C or higher, and even more preferably 150 °C or higher.
- In the present disclosure, a lower limit of a holding time during the tempering is not particularly limited. However, when the holding time during the tempering is less than 1.9t + 10 minutes (t: plate thickness (mm)), a thickness center portion compared to the surface thereof may not be sufficiently heated, as the heat treatment is performed at a relatively low temperature for a short time. Therefore, the holding time during the tempering is preferably 1.9t + 10 minutes (t: plate thickness (mm)) or more. The holding time during the tempering is more preferably 1.9t + 12 minutes (t: plate thickness (mm)) or more, more preferably 1.9t + 15 minutes (t: plate thickness (mm)) or less, and most preferably 1.9t + 20 minutes (t: plate thickness (mm)) or more.
- After tempering, it can be cooled to room temperature by air cooling. Through such a tempering process, the hot-rolled steel sheet according to an aspect of the present disclosure may have softened tempered martensite as a base structure.
- The hot-rolled steel sheet obtained through the above-described series of manufacturing processes is a steel material having a thickness of 6 to 40 mm, and can provide excellent bullet-proof resistance by securing high hardness and high toughness.
- Hereinafter, bullet-proof steel of the present disclosure and a method for manufacturing the same will be described in more detail through specific examples. It should be noted that the following examples are only for understanding of the present disclosure, and are not intended to specify the scope of the present disclosure. The scope of the present disclosure may be determined by the matters described in the claims and the matters reasonably inferred therefrom.
- After preparing a steel slab having alloy compositions of Table 1 below, [heating - rolling - heat treatment (quenching) - heat treatment (tempering)] were performed according to process conditions illustrated in Table 2 below to manufacture each hot-rolled steel sheet. In this case, after being water cooled to a cooling end temperature, air cooling was applied to room temperature. The tempering performed thereafter also applied air cooling to room temperature after performing a heat treatment at a specific temperature. Alloy compositions not listed in Table 1 refer to unavoidable impurities and iron (Fe). In addition, a part marked with"-" in Table 1 means that the corresponding component was not intentionally added, which is preferable to be interpreted as 0% by weight within an error range. Specimen 11 in Table 2 refers to a specimen that was not subjected to the second heat treatment (tempering) after the first heat treatment (quenching).
[Table 1] St ee 1 ty pe Alloy composition(weight %) Relation al Expressi on 1 C Si Mn P* S* Ni Cr Mo Nb V Al Ca* Ti B* N* A 0.3 6 1.3 7 1.4 5 76 19 1.1 3 0.6 8 0.2 8 0.0 3 - 0.0 4 16 0.01 2 21 45 4.93 B 0.1 6 0.2 9 1.0 8 72 20 0.4 2 0.4 6 0.1 3 0.0 1 0.0 2 0.0 3 18 0.01 7 23 48 0.46 C 0.2 4 1.3 9 1.1 2 73 18 0.9 6 0.5 5 0.3 9 0.0 2 - 0.0 3 22 - 21 44 3.34 D 0.2 0 1.6 5 1.2 76 19 1.1 4 0.8 1 0.4 4 0.0 3 0.0 4 0.0 3 21 - 19 46 3.30 E 0.2 3 1.2 6 0.9 6 77 17 1.0 6 0.7 3 0.4 2 0.0 3 - 0.0 3 19 0.01 5 18 46 2.90 F 0.1 8 1.1 2 0.6 3 80 18 0.7 1 0.6 2 0.2 7 0.0 2 - 0.0 3 20 0.01 4 20 43 2.02 P*, S*, Ca*, B*, and N* are represented in units of ppm [Table 2] Spe cim en No. Stee 1 type Thic knes s (mm) Slab heatin 9 (°C) Rolling Primary heat treatment (quenching) Secondary heat treatment (tempering) Rough rollin 9 (°C) Finish hot rollin 9 (°C) Heati ng tempe ratur e (°C) Resid ence time (min. ) Cooli ng end tempe ratur e (°C) Coolin g rate (°C/s) Heating tempera ture (°C) Holdin g time (min.) 1 A 10 1147 1055 861 909 36 30 65.2 208 39 2 A 25 1149 1029 928 913 54 37 45.9 227 60 3 A 50 1155 1044 910 904 85 23 12.5 212 95 4 B 15 1162 1025 899 907 43 24 44.1 301 39 5 B 30 1148 1035 923 905 60 32 31.9 254 75 6 B 60 1153 980 915 904 89 43 7.6 203 114 7 C 8 1185 1059 886 913 32 19 62.2 215 36 8 C 25 1129 1033 925 916 54 25 43.3 391 60 9 C 50 1131 965 911 907 86 21 9.4 224 116 10 D 12 1145 1046 924 905 40 18 50.5 209 45 11 D 25 1138 1030 922 914 55 19 40.7 - - 12 D 40 1149 991 916 900 72 20 25 216 93 13 D 60 1142 984 900 912 93 285 7.7 200 127 14 E 20 1163 1030 934 917 47 30 43.8 209 59 15 E 40 1154 1004 927 903 75 25 20.6 231 97 16 E 40 1152 1018 923 912 74 29 21.9 208 15 17 E 60 1120 977 909 906 100 16 7.1 220 140 18 F 40 1145 982 914 908 85 41 9.0 256 118 - Thereafter, a microstructure and mechanical properties of each hot-rolled steel sheet were measured, and the results thereof were shown in Table 3.
- The microstructure of each hot-rolled steel sheet was cut into an arbitrary size as a specimen to manufacture a mirror surface, a Nital etching solution was used to corrode the specimen, and then an optical microscope and a scanning electron microscope (SEM) were used to observe a 1/2t point which was a thickness center part. In this case, a fraction of the microstructure was measured by electron back-scattered diffraction (EBSD) analysis.
- In addition, hardness and toughness of each hot-rolled steel sheet were measured using a Brinell hardness tester (load: 3000 kgf, 10 mm tungsten injection port) and a Charpy impact tester, respectively. In this case, in the surface hardness, an average value of three measurements after a milling process of the surface of the hot-rolled sheet at 2 mm was used, and in the Charpy impact test, a specimen was collected at 1/4t point in the thickness direction, and then an average value of three measurements at -40°C was used.
[Table 3] Specim en Steel type Microstructure (area %) Surface hardness Impact toughness (J, @-40°C) No. TM B R-γ (HB) 1 A 98 - 2 526 24 2 A 97 - 3 493 28 3 A 98 - 2 511 26 4 B 99 - 1 329 29 5 B 97 - 3 337 34 6 B 98 - 2 355 31 7 C 96 - 4 424 45 8 C 100 - 0 308 63 9 C 97 - 3 417 37 10 D 96 - 4 379 58 11 D 100 - 0 470 20 12 D 97 - 3 409 33 13 E 53 B: 47 0 302 77 14 E 97 - 3 435 32 15 E 97 - 3 414 34 16 E 100 - 0 461 24 17 E 96 - 4 416 40 18 F 98 - 2 347 30 TM: Tempered martensite, B: Bainite, R-γ: Retained austenite - As shown in Tables 1 to 3, it can be seen that specimens satisfying the alloy composition and process conditions of the present disclosure have a surface harness of 360 to 440 HB and an impact absorption energy of 27 J or more at -40°C, but specimens not satisfying at least one of the alloy compositions or process conditions of the present disclosure do not have a surface hardness of 360 to 440 HB or an impact absorption energy of 27 J or more at -40°C at the same time.
- While example embodiments have been shown and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.
Claims (9)
- A high-hardness bullet-proof steel having excellent low-temperature impact toughness comprising, by weight: 0.18 to 0.25% of carbon (C), 1.0 to 2.0% of silicon (Si), 0.5 to 1.6% of manganese (Mn), 0.5 to 1.2% of nickel (Ni), 0.4 to 1.5% of chromium (Cr), 0.05% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.006% or less of nitrogen (N), 0.07% or less of aluminum (Al) (excluding 0%), 0.1 to 0.5% of molybdenum (Mo), 0.01 to 0.05% of niobium (Nb), 0.0002 to 0.005% of boron (B), 0.0005 to 0.004% of calcium (Ca), with a balance of iron (Fe) and inevitable impurities, satisfying the following [Relational Expression 1], wherein a tempered martensite base structure including retained austenite is included as a microstructure,
- The high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 1, wherein the bullet-proof steel further comprises, by weight:
at least one of 0.005 to 0.025% of titanium (Ti) and 0.2% or less of vanadium (V). - The high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 1, wherein a fraction of the tempered martensite is 90% or more by area, and a fraction of the retained austenite is 0.5% by area to 5% by area.
- The high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 1, wherein the bullet-proof steel has a surface hardness of 360 to 440 HB and an impact absorption energy of 27 J or more at -40°C.
- The high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 1, wherein the bullet-proof steel has a thickness of 6 to 40 mm.
- A manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness, comprising operations of: preparing a steel slab including, by weight: 0.18 to 0.25% of carbon (C), 1.0 to 2.0% of silicon (Si), 0.5 to 1.6% of manganese (Mn), 0.5 to 1.2% of nickel (Ni), 0.4 to 1.5% of chromium (Cr), 0.05% or less of phosphorus (P), 0.02% or less of sulfur (S), 0.006% or less of nitrogen (N), 0.07% or less of aluminum (Al) (excluding 0%), 0.1 to 0.5% of molybdenum (Mo), 0.01 to 0.05% of niobium (Nb), 0.0002 to 0.005% of boron (B), 0.0005 to 0.004% of calcium (Ca), with a balance of iron (Fe) and inevitable impurities, satisfying the following [Relational Expression 1];heating the steel slab in a temperature range of 1050 to 1250 °C;rough rolling the heated steel slab in a temperature range of 950 to 1150 °C;subjecting the heated steel slab to finish hot rolling in a temperature range of 850 to 950 °C after the rough rolling to manufacture a hot-rolled steel sheet;performing a primary heat treatment of heating the hot-rolled steel sheet to a temperature range of 880 to 930 °C and then cooling the same to a cooling end temperature of 150 °C or lower at a cooling rate of 10 °C/s or more; andperforming a secondary heat treatment of heating the primarily heat-treated hot-rolled steel sheet to a temperature range of 350 °C or lower and maintaining the same,in Relational Expression 1, [C] and [Si] refer to contents (weight %) of carbon (C) and silicon (Si) included in the steel slab, and 0 is substituted when the corresponding element is not intentionally added.
- The manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 6, wherein the steel slab further comprises, by weight: at least one of 0.005 to 0.025% of titanium (Ti) and 0.2 % or less of vanadium (V).
- The manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 6, wherein a residence time during the primary heat treatment is 1.3t + 10 minutes (t: plate thickness (mm)) or more.
- The manufacturing method for a high-hardness bullet-proof steel having excellent low-temperature impact toughness of claim 6, wherein a holding time during the secondary heat treatment is 1.9t + 10 minutes (t: plate thickness (mm)) or more.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020200179081A KR102498147B1 (en) | 2020-12-18 | 2020-12-18 | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof |
PCT/KR2021/015867 WO2022131535A1 (en) | 2020-12-18 | 2021-11-04 | High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same |
Publications (1)
Publication Number | Publication Date |
---|---|
EP4265785A1 true EP4265785A1 (en) | 2023-10-25 |
Family
ID=82059642
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP21906840.0A Pending EP4265785A1 (en) | 2020-12-18 | 2021-11-04 | High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same |
Country Status (4)
Country | Link |
---|---|
EP (1) | EP4265785A1 (en) |
KR (1) | KR102498147B1 (en) |
AU (1) | AU2021400778A1 (en) |
WO (1) | WO2022131535A1 (en) |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5365216B2 (en) * | 2008-01-31 | 2013-12-11 | Jfeスチール株式会社 | High-strength steel sheet and its manufacturing method |
JP5136609B2 (en) * | 2010-07-29 | 2013-02-06 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet excellent in formability and impact resistance and method for producing the same |
CN103205627B (en) * | 2013-03-28 | 2015-08-26 | 宝山钢铁股份有限公司 | A kind of Low-alloy high-performance wear-resistant steel plate and manufacture method thereof |
CN103205634B (en) * | 2013-03-28 | 2016-06-01 | 宝山钢铁股份有限公司 | A kind of low-alloy high hardness wear-resisting steel plate and manufacture method thereof |
CN105088090A (en) | 2015-08-28 | 2015-11-25 | 宝山钢铁股份有限公司 | Armor plate with tensile strength being 2000 MPa and manufacturing method thereof |
KR102031446B1 (en) * | 2017-12-22 | 2019-11-08 | 주식회사 포스코 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
KR102119959B1 (en) * | 2018-09-27 | 2020-06-05 | 주식회사 포스코 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
-
2020
- 2020-12-18 KR KR1020200179081A patent/KR102498147B1/en active IP Right Grant
-
2021
- 2021-11-04 EP EP21906840.0A patent/EP4265785A1/en active Pending
- 2021-11-04 AU AU2021400778A patent/AU2021400778A1/en active Pending
- 2021-11-04 WO PCT/KR2021/015867 patent/WO2022131535A1/en unknown
Also Published As
Publication number | Publication date |
---|---|
AU2021400778A1 (en) | 2023-07-06 |
AU2021400778A9 (en) | 2024-06-20 |
WO2022131535A1 (en) | 2022-06-23 |
KR102498147B1 (en) | 2023-02-08 |
KR20220088239A (en) | 2022-06-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2940171B1 (en) | High-manganese wear resistant steel having excellent weldability and method for manufacturing same | |
KR20140084772A (en) | Non-quenched and tempered steel wire rod having excellent toughness and manufacturing method thereof | |
KR20190075378A (en) | High-strength wire rod and steel with excellent hydrogen retardation resistance and manufacturing the same | |
EP3392364B1 (en) | High hardness abrasion resistant steel with excellent toughness and cutting crack resistance, and method for manufacturing same | |
KR101819383B1 (en) | Quenched high carbon steel sheet and method for manufacturing the same | |
EP4265789A1 (en) | Armored steel having high hardness and excellent low-temperature impact toughness, and method for manufacturing same | |
EP4265790A1 (en) | Armored steel having high hardness and excellent low-temperature impact toughness and manufacturing method therefor | |
EP4265788A1 (en) | High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same | |
EP4265785A1 (en) | High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same | |
EP4265786A1 (en) | High hardness armored steel having excellent low-temperature impact toughness, and manufacturing method therefor | |
EP4265791A1 (en) | Armored steel having high hardness and excellent low-temperature impact toughness, and method for manufacturing same | |
KR102498158B1 (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
KR20210079482A (en) | Steel sheet having excellent ductility and low-temperature impact toughness and method for manufacturing thereof | |
KR102498156B1 (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
KR102498155B1 (en) | Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof | |
KR20200075456A (en) | High carbon boron added steel and manufacturing method thereof | |
EP4386104A1 (en) | High-hardness bulletproof steel having excellent low-temperature toughness, and manufacturing method therefor |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20230712 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
DAV | Request for validation of the european patent (deleted) | ||
DAX | Request for extension of the european patent (deleted) |