CN107794460B - A kind of enamel high-strength steel sheet and its manufacturing method with excellent two-sided application of slip performance - Google Patents
A kind of enamel high-strength steel sheet and its manufacturing method with excellent two-sided application of slip performance Download PDFInfo
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- CN107794460B CN107794460B CN201610784710.7A CN201610784710A CN107794460B CN 107794460 B CN107794460 B CN 107794460B CN 201610784710 A CN201610784710 A CN 201610784710A CN 107794460 B CN107794460 B CN 107794460B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 139
- 239000010959 steel Substances 0.000 title claims abstract description 139
- 210000003298 dental enamel Anatomy 0.000 title claims abstract description 89
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 26
- 239000002245 particle Substances 0.000 claims abstract description 59
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 41
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 23
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 18
- 230000002427 irreversible effect Effects 0.000 claims abstract description 16
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 14
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 11
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 239000013078 crystal Substances 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 18
- 238000001816 cooling Methods 0.000 claims description 16
- 238000002791 soaking Methods 0.000 claims description 11
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 6
- 229910001562 pearlite Inorganic materials 0.000 claims description 5
- 238000005507 spraying Methods 0.000 claims description 5
- 229910001567 cementite Inorganic materials 0.000 claims description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 4
- 241001417490 Sillaginidae Species 0.000 claims description 2
- 239000010936 titanium Substances 0.000 description 32
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 25
- 229910052739 hydrogen Inorganic materials 0.000 description 25
- 239000001257 hydrogen Substances 0.000 description 25
- 238000003860 storage Methods 0.000 description 25
- 238000000034 method Methods 0.000 description 19
- 229910052799 carbon Inorganic materials 0.000 description 15
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 14
- 238000010304 firing Methods 0.000 description 14
- 239000010955 niobium Substances 0.000 description 13
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 12
- 241000251468 Actinopterygii Species 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 10
- 239000011572 manganese Substances 0.000 description 9
- 230000008569 process Effects 0.000 description 9
- 238000001556 precipitation Methods 0.000 description 8
- 230000009466 transformation Effects 0.000 description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 7
- 239000002320 enamel (paints) Substances 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 7
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 7
- 239000000243 solution Substances 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 238000005275 alloying Methods 0.000 description 6
- 150000001875 compounds Chemical class 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- 239000011651 chromium Substances 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 238000013461 design Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000011521 glass Substances 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 239000004411 aluminium Substances 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 239000008187 granular material Substances 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 238000004090 dissolution Methods 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 3
- 230000002195 synergetic effect Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 239000005864 Sulphur Substances 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000010813 municipal solid waste Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000010583 slow cooling Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 230000022972 amelogenesis Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 230000008676 import Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 238000009940 knitting Methods 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000003960 organic solvent Substances 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000009290 primary effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005488 sandblasting Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 235000012239 silicon dioxide Nutrition 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- 239000011800 void material Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- 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
- C21D2211/003—Cementite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a kind of enamel high-strength steel sheets with excellent two-sided application of slip performance, its chemical element mass percent are as follows: C:0.06~0.15%, Si:0.16~0.50%, Mn:0.6~2.0%, S:0.010~0.035%, Al:0.001~0.05% and Als≤0.05%, Ti:0.15~0.25%, N:0.0035~0.010%, Nb:0~0.10%, surplus are Fe and other inevitable impurity；The enamel uses the microstructure of high-strength steel sheet to have ferrite and a TiN particle as precipitated phase, and the surface of the TiN particle is in plane, is formed with irreversible small hole between the TiN particle and surface ferrite crystal grain in curved surface.Correspondingly, the invention also discloses the manufacturing methods of the enamel high-strength steel sheet described in one kind.The two-sided application of slip performance of enamel high-strength steel sheet of the present invention is good, and no squama is quick-fried, and intensity is high.
Description
Technical field
The present invention relates to a kind of high-strength steel sheet and its manufacturing method more particularly to a kind of enamel high-strength steel sheet and
Its manufacturing method.
Background technique
Enamel technique is exactly that the nature of glass enamel containing high silicon dioxide component is coated in after machine-shaping
Steel matrix surface, one kind that then enamel is firmly bonded to steel matrix surface formation composite material after high temperature sintering add
Work process, this composite material have the Common advantages such as the stability of glass and the intensity of steel, have good wearability, to each
Kind acid, alkali, organic solvent have preferable corrosion resistance.Enamel technique is mainly used for glass-lined equipment and enamel accessory
Such as glassed steel reaction vessels, enamel storage tank, enamel glass stirrer are fabricated, petrochemical industry, system doctor's pharmacy etc. are widely used in
Industry.Glass-lined equipment generally uses the single side application of slip, and enamel accessory mostly uses the two-sided application of slip or wraps up the application of slip entirely.Enamel
Industry has more than 60 years history in Chinese development, especially in recent years, with advanced application of slip technology and firing technology in the world
Introducing and both at home and abroad high-end enamel development and application, China gradually becomes the manufacture of glass-lined equipment in the world and accessory
The total quality of big country, glass-lined equipment increases.
But, incompatible with the production-scale rapid growth of glass-lined equipment, enamel is still with steel plate at present
Based on the ordinary constructions such as Q235, Q245R and Q345R steel plate and steel plate of pressure vessel.The prior art can not be solved fundamentally
Squama quick-fried problem is also easy to produce during enamel, and the prior art can not be used for glass lined stirring blade, ring flange etc.
Need to wrap up the enamel accessory of the application of slip entirely, in addition, there is also be difficult to overcome air blister defect, firing deformation etc. serious for the prior art
The problem of influencing product quality.Even if when although domestic only some steel plate specials alleviate the application of slip when being used for the single side application of slip
There is the quick-fried risk of squama, but when being used for the two-sided application of slip also it is difficult to ensure that not generating the defects of squama is quick-fried.
With the continuous development of enamel industry, the total quality of glass-lined equipment and enamel accessory is required increasingly to mention
Height, relate generally to three aspect close fit problem, i.e., the improvement of glaze quality, the improvement of firing process and have it is excellent comprehensive
Close being adapted for performance steel plate.The requirement of comprehensive performance increasingly improves: anxious to the corrosion resistance, wearability and heatproof of enamel enamel coating
Become performance requirement to improve, the matching of steel plate and enamel coating is required to increase accordingly: for example, the application of slip and firing number are reduced, it must
The anti-bubbling ability and high temperature deformation resistance ability of steel plate must be improved.
The fish scaling resistance of steel plate is improved for the hot rolled steel plate of the two-sided application of slip in the prior art, it is main using addition
A large amount of titanium, and improve the ratio of Ti/C, for example, Ti mass percent be 0.09~0.20%, Ti/C ratio be 1.5~
3.0 or even Ti/C ratio 5~15 etc..Purpose using this kind of method is that a large amount of tiny TiC particles are formed in steel, is relied on
TiC particle becomes storage hydrogen trap, to prevent the generation squama during application of slip quick-fried.But even with so high Ti and Ti/C
Than, or even sometimes also need that the expensive alloying element such as a large amount of niobium, vanadium, chromium is added, it also can only be to a certain extent
The fish scaling resistance for improving steel plate is difficult fundamentally to solve the problems, such as that generation squama is quick-fried in the two-sided application of slip.Generate above-mentioned ask
The reason of topic, can be attributed to, since firing temperature high (up to 930 DEG C or so), the firing time of enamel technique are long, and
And need to be by being repeatedly burnt into repeatedly, the precipitation of phase transformation and TiC to steel generates strong influence.Firing temperature is in TiC dissolution
Sensitivity interval with precipitation be also phase transformation occur section, TiC is extremely unstable in this section, during heating can all or
Major part is dissolved in subsequent cooling to be precipitated again, simultaneously because cooling rate is slower, TiC particle can become larger, the storage thus generated
Hydrogen trap gradually decreases.In addition, the slight void between TiC particle and steel matrix also can as phase transformation and precipitated phase are with progress
It is gradually reduced and even disappears, storage hydrogen trap is caused to decline to a great extent.
Because of this it may be desirable to a kind of enamel high-strength steel sheet be obtained, with excellent two-sided application of slip performance.
Summary of the invention
One of the objects of the present invention is to provide a kind of enamel high-strength steel sheet with excellent two-sided application of slip performance,
It is quick-fried squama is not generated in the two-sided application of slip, and intensity with higher, good plasticity and welding performance.
Based on foregoing invention purpose, the present invention provides a kind of, and the enamel with excellent two-sided application of slip performance is high-intensitive
Steel plate, chemical element mass percent are as follows: C:0.06~0.15%, Si:0.16~0.50%, Mn:0.6~2.0%, S:
0.010~0.035%, Al:0.001~0.05% (or Als≤0.05%), Ti:0.15~0.25%, N:0.0035~
0.010%, Nb:0~0.10%, surplus are Fe and other inevitable impurity；
The enamel uses the microstructure of high-strength steel sheet to have ferrite and the TiN particle as precipitated phase, should
The surface of TiN particle is in plane, is formed between the TiN particle and surface ferrite crystal grain in curved surface irreversible small
Hole.
Inventor through a large number of experiments and test, find thermal deformation processing and cold deformation to storage hydrogen trap and
Other performance influence has the characteristics that significantly different, that is to say, that steel plate is after cold working (such as cold rolling) deformation in tiny analysis
A large amount of small hole is more prone to produce around phase out, these small holes are permanent, irreversible storage hydrogen traps, but heat
The steel plate of (such as hot rolling) is processed due to being influenced by factors such as phase transformation, recrystallizations, then is hardly formed around tiny precipitated phase
Largely, permanent storage hydrogen trap.Inventor's discovery other than depending on the factors such as processing temperature and deflection, equally at
Divide and the cold working steel plate of tissue is compared with hot-working steel plate, the raw largely irreversible storage hydrogen trap of hot-working steel plate relatively difficult labour,
Therefore hot-working steel plate is more prone to produce the quick-fried phenomenon of squama in the application of slip, that is to say, that the fish scaling resistance specific heat that steel plate is cold worked adds
The fish scaling resistance of work steel plate is more excellent.It should be pointed out that hot-working steel plate only relies on a large amount of alloying element of addition to be precipitated
A large amount of second phase particles are also difficult fundamentally to improve its fish scaling resistance.
Inventor is based on this discovery as a result, while sufficiently taking into account enamel steel to scaling resistance, adherence
Property, the comprehensive performances such as anti-needle pore defect and intensity, plasticity, toughness and weldability matching requirement, in alloying element and processing
After having carried out a large amount of research and experimental contrast analysis in terms of the matching of technological parameter, it is reasonable to be carried out by the chemical component to steel
Design utilize the synergistic effect of each chemical element, creativeness proposes the mass percent for controlling each chemical element, especially
It is the mass percent of Ti and N, to obtain the relatively fine TiN particle of precipitated phase, and forms irreversible storage using the particle
Hydrogen trap.The surface of the TiN particle is in plane, is formed between the TiN particle and surface ferrite crystal grain in curved surface
Irreversible small hole.Since the TiN particle is all even to be precipitated in molten steel at high operating temperatures, and add in heat
It is substantially insoluble during work, and overwhelming majority TiN particle will not be dissolved in firing range, therefore, these
Small hole is beneficial irreversible storage hydrogen trap.
It should be noted that in the technical scheme, the precipitated phase for forming storage hydrogen trap is not limited in TiN, except TiN with
Outside, there are also other precipitated phases can also form storage hydrogen trap, such as complex chemical compound (Ti, Nb) (C, N).In another example spherical in shape
The TiS and TiC of particle, however the storage hydrogen trap effect of these precipitates is good without TiN.
And enamel in the prior art with steel by control Ti/C ratio (as control Ti/C in 1~4 range) from
And TiC particle being precipitated, and form storage hydrogen trap around its particle, this makes the prior art have following defects that form storage hydrogen
Trap is more difficult, and since TiC precipitation or solution temperature are lower, is easy so that it is formed by storage hydrogen trap by hot-working or height
The influence of temperature firing is significant, causes the fluctuation and variation of hydrogen storage performance.And technical solutions according to the invention pass through TiN particle institute
The small hole formed overcomes drawbacks described above as irreversible storage hydrogen trap, uses to improve enamel of the present invention
The two-sided application of slip performance of high-strength steel sheet.
The design principle of each chemical element of enamel high-strength steel sheet of the present invention is as follows:
Carbon: carbon is to ensure that the key element of armor plate strength, and the mass percent of carbon increases, and intensity rises, plasticity and toughness
Decline.Carbon and titanium generate TiC particle, can not only strengthen matrix, reduce the pearlitic structrure in steel, and the storage to steel is improved
Hydrogen Energy power is also helpful.Therefore, it is limited in the mass percent of the carbon of enamel of the present invention high-strength steel sheet
0.06~0.15%.But as described above, since firing temperature is high in the enamel technical process of steel, the time is long, and
And it will be by being repeatedly repeated, so that the phase transformation of steel and recrystallizing molten and precipitation is in the temperature being close with the weight of TiC particle
In range, therefore TiC particle is extremely unstable in steel, therefore the TiC particle in the present invention is having for irreversible storage hydrogen trap
Benefit supplement, is not the precipitate for playing primary effect, and the technical program mainly or by the ingredient design of other elements obtains
Stable, effective, irreversible small hole is obtained as storage hydrogen trap to realize technical effect.
Silicon: silicon plays solution strengthening effect in steel, while silicon can also improve the high temperature deformation resistance ability of steel, coordinates steel plate
The difference of anti-dilatancy ability between enamel layer is advantageous for the heatproof shock property for improving steel plate and enamel interlayer.
In general, under by sandblasting, warding off the normal process of ground coat enamel, ground coat enamel mainly plays close between increase steel plate and overglaze steel plate
Effect, can guarantee excellent adhesion property completely in the case where there is ground coat enamel, therefore suitable silicon is added in steel will not shadow
Ring the adhesion property between steel plate and enamel.But the mass percent of silicon is higher than 0.50% can be to performances such as the plasticity of steel and toughness
It is unfavorable, also it is unfavorable for welding.For this purpose, the mass percent control of the silicon of enamel high-strength steel sheet of the present invention exists
0.16~0.50%.
Manganese: manganese is to strengthen matrix element, therefore the purpose that manganese is added essentially consists in the intensity for improving steel, but the quality hundred of manganese
When dividing than being higher than 2.0%, the plasticity of steel can be seriously reduced.In addition, manganese is in steel and reaction of Salmon-Saxl generates manganese sulfide, in general steel
Manganese sulfide is in hairline shape, extremely harmful to the horizontal plastic property and toughness of steel plate, however, in enamel of the present invention with high-strength
It spends in steel plate, due to there is the addition of appropriate titanium, manganese is mainly precipitated with spherical (Mn, Ti) S, it is entirely avoided simple manganese sulfide
It is precipitated and its adversely affects.In consideration of it, the mass percent of the manganese of enamel of the present invention high-strength steel sheet is limited to
0.60~2.0%.
Aluminium: aluminium is strong deoxidant element, since oxygen and titanium react easily in molten steel and forms field trash, consumes effective titanium,
Therefore, it is necessary to add aluminium to carry out deoxidation, to reduce the oxygen content in steel.Enamel high-strength steel sheet of the present invention
The mass percent control of aluminium controls Als≤0.05% 0.001~0.05%.
Titanium and niobium: titanium and niobium are all strong carbon, nitride forming element.It is compared with titanium, niobium and nitrogen are precipitated to be formed in high temperature
NbN and more stable precipitated phase, but its particle size ratio TiN is thin, it can be to avoid the adverse effect of coarse TiN.With this
Meanwhile niobium can also form tiny NbC particle with carbon, and the intensity of steel can be improved.Therefore, it adds titanium and on the one hand niobium guarantees
There are enough second phase particles to be precipitated, on the other hand can also avoid the formation of more coarse TiN particle.In addition, extra titanium
It can react with carbon, generate relatively fine TiC particle.In consideration of it, enamel high-strength steel sheet of the present invention
Mass percent of the mass percent control of Ti in 0.15~0.25%, Nb is controlled 0~0.10%.
Nitrogen and sulphur: in technical solutions according to the invention, alloying element Ti can form compound with C, S and N.This skill
Art scheme is by forming comparatively fine TiN particle and TiS particle, to form irreversible storage hydrogen trap.Therefore, institute of the present invention
The mass percent of nitrogen and sulphur limits in the enamel high-strength steel sheet stated are as follows: and 0 < S≤0.035%, N:0.0035~
0.010%.
In addition, it is necessary to illustrate, inevitably impurity is primarily referred to as P element, the technical program in the technical program
It can control P≤0.025% or less.
Further, in enamel high-strength steel sheet of the present invention, meet 4.5 × 10-2≤1.5×S+
3.43×N≤8.5×10-2, wherein S and N respectively indicates the mass percent of corresponding element；The microstructure also has conduct
The TiS particle of precipitated phase, the TiS particle is spherical in shape, and the TiS particle is used to form irreversible small hole.Namely
Say that S and N are substituted into formula numerical value is the numerical value before percentage sign, for example, S mass percent be 0.019% embodiment in, should
The substitution numerical value of S is exactly 0.019 in formula.
In order to further improve the comprehensive performance of steel, its fish scaling resistance, plasticity and toughness, this case invention are especially improved
People has carried out further restriction to the synergistic effect chemical element each in this case technical solution, meets 4.5 × 10-2≤
1.5×S+3.43×N≤8.5×10-2, wherein S and N respectively indicates the mass percent of corresponding element.Its design principle are as follows: steel
Middle alloying element Ti can form compound with C, S and N.Typically, since the Precipitation Temperature of TiN particle is high, particle is coarse
The plasticity and toughness of steel can be damaged.Thus, by reducing the mass percent of nitrogen, to avoid or reduce coarse TiN particle, (such as long side is big
In 5 μm) precipitation.However, in the inventive solutions, in order to improve the performance of steel, inventor further passes through control N
Allow to be precipitated comparatively fine so that limitation forms the precipitation quantity and temperature of TiN and TiS with the mass percent of S
(side length is less than 3 μm) TiN particle and TiS particle.The hard phase TiN that these high temperature can be made to be precipitated is brought using this kind of mode
And TiS, it is substantially insoluble in hot procedure, so that more obvious small sky can be formed between TiN particle and the matrix of steel
Hydrogen trap is store in cave, will not be dissolved the overwhelming majority TiN and TiS particle granules even if in corresponding firing range
Fall.Meanwhile passing through before hot-working when being heated to slab and improving heating temperature and extend soaking time, so that TiN
Particle granules a part dissolution, especially TiN preferentially at its grain corner or peripheral portion dissolution, make TiN particle granules
Attenuate, it is advantageous to the plasticity and toughness that improve steel, while more tiny particle can be precipitated in the part TiN particle granules dissolved,
To increasing later, storage hydrogen trap is also highly beneficial, to improve the fish scaling resistance of steel.In addition, the mass percent mistake of N, S
It will form a large amount of field trash when high.
Further, in enamel high-strength steel sheet of the present invention, meet 0.20%≤Ti+ (48*Nb/
93)≤0.25%.
In order to further improve the comprehensive performance of steel, its fish scaling resistance is especially improved, inventor is to this case skill
Synergistic effect in art scheme between each chemical element has carried out further restriction, meets 0.20%≤Ti+ (48*Nb/93)
≤ 0.25%, wherein Ti and Nb respectively indicates the mass percent of corresponding element.The formula also helps the titanium so that sufficient amount
With the strong carbon, nitride forming element such as niobium, the carbon and nitrogen in steel are almost secured, more carbon is not had especially and is formed
Pearlitic structrure, in this way by inhibit pearlitic structrure generation, avoid during hot procedure and high temperature enamel firing due to
Decomposition and the Solid State Transformation of pearlite repeatedly and the high temperature deformation for leading to steel plate.
Further, in enamel high-strength steel sheet of the present invention, also contain Cu:0.01~0.10%,
At least one of Mo:0.005~0.10%, Cr:0.01~0.10% and Ni:0.01~0.10%.
Adding alloying element is to further improve the enamel of the present invention with excellent two-sided application of slip performance
With the performance of high-strength steel sheet, design principle is:
Copper: a small amount of copper is deposited in surface of steel plate and is conducive to improve the adherence between steel plate and enamel coating, it is quick-fried to improve anti-squama
Performance.When copper content improves, the intensity of steel is also improved.In consideration of it, copper in enamel high-strength steel sheet of the present invention
Mass percent is limited to 0.01~0.10%.
Molybdenum: molybdenum is conducive to improve the adherence between steel and glass enamel coating, can also improve the high temperature resistant deformability of steel.
But mass percent is excessively high to will increase cost.Therefore, enamel of the present invention is limited to 0.005 with molybdenum in high-strength steel sheet
~0.10%.
Chromium: chromium is conducive to improve the adherence between steel plate and enamel coating, improves fish scaling resistance.For this purpose, of the present invention
Enamel be limited to 0.01~0.10% with chromium in high-strength steel sheet.
Nickel: nickel not only improves the adherence improved between steel plate and enamel coating, improves fish scaling resistance, meanwhile, nickel can be with
Improve the low temperature impact properties of steel plate.But when nickel is more than 0.10%, cost is not only increased, but also can hinder between steel plate and enamel coating
Reaction, can reduce adhesion property.For this purpose, enamel of the present invention be limited to 0.01 with nickel in high-strength steel sheet~
0.10%.
Further, in enamel high-strength steel sheet of the present invention, microstructure is ferrite+pearlite
Or ferrite+cementite, the Phase Proportion of medium pearlite or cementite are 0-10%.
Further, in enamel high-strength steel sheet of the present invention, ferritic average crystal grain diameter is little
In 20 μm.
Further, in enamel high-strength steel sheet of the present invention, yield strength >=345MPa, tension is strong
Degree >=450MPa, elongation percentage >=26%.
Another object of the present invention is to provide the manufacturing methods of the enamel high-strength steel sheet described in one kind, successively
Comprising steps of
(1) it smelts and casts；
(2) hot rolling: the heating temperature before slab rolling is 1150~1250 DEG C, soaking time=t × (0.5~1.5),
Middle t is slab thickness, and unit mm, the unit of soaking time is min；1100~1200 DEG C of roughing rolling temperature of control, deformation
Amount >=50%；Water-spraying control after roughing, control finish rolling start rolling temperature are 920~1000 DEG C, and finishing temperature is 870~920 DEG C,
Deflection >=60%；
(3) cooling.
In the manufacturing method of the enamel high-strength steel sheet of the present invention with excellent two-sided application of slip performance, it is
Guarantee that enamel high strength steel has excellent fish scaling resistance, manufacturing method control process flow of the present invention is special
It is not each technological parameter in course of hot rolling, makes steel plate that there is ferrite and the TiN particle as precipitated phase, the TiN particle
Surface be in plane, be formed with irreversible small hole between the TiN particle and surface ferrite crystal grain in curved surface.
In step (2), slab rolling before heating temperature be 1150~1250 DEG C and soaking time=t × (0.5~
1.5), wherein t is slab thickness, and unit mm, the unit of soaking time is min, be because are as follows: be on the one hand to obtain uniform
The austenite structure of change is partly dissolved the compound of titanium.Wherein, the calculation of soaking time are as follows: for example,
Slab thickness is 230mm, then soaking time is 115~345min.
In addition, 1100~1200 DEG C of roughing rolling temperature of the control in step (2), deflection >=50% is for hot rolling
Process carries out in austenite recrystallization section, to pass through repeat-rolling fining austenite grains.
At the same time, in step (2), water-spraying control after roughing, control finish rolling start rolling temperature is 920~1000 DEG C,
Finishing temperature is 870~920 DEG C, deflection >=60%, it is ensured that phase transformation can be sufficiently completed after rolling.Meanwhile it is logical
It crosses using deflection >=60%, so that forming a large amount of small hole in TiN particle periphery.
In step (3), cooling can take water cooling or slow cooling.
Further, in manufacturing method of the present invention, in the step (3), the average cooling rate of control≤
10℃/s。
In manufacturing method of the present invention, control average cooling rate≤10 DEG C/s be because are as follows: in cooling procedure,
The titanium and carbon of solid solution can be precipitated in the form of compound, be evenly distributed in matrix in small and dispersed state, to reduce pearl
In flakes, and by controlling cooling rate, the ferritic structure in steel is refined for the transformation of body of light and pearlite aggregation.It is cooling
When rate is higher than 10 DEG C/s, the compound for being unfavorable for titanium is sufficiently precipitated, and will form residual stress in steel, causes to cause group
The problems such as knitting unevenness.Therefore, step (3) controls average cooling rate≤10 DEG C/s in manufacturing method of the present invention.
It further, further include step (4) normalizing in manufacturing method of the present invention.
In manufacturing method of the present invention, normalized treatment is in order to keep the Carbide Precipitation in steel more abundant, together
When normalized treatment can also homogenize ferritic structure, completely eliminate internal residual stress.
Further, in manufacturing method of the present invention, in the step (4), control normalizing temperature 930~
980℃。
Enamel of the present invention with excellent two-sided application of slip performance has good anti-squama quick-fried with high-strength steel sheet
Performance, two-sided application of slip function admirable.In addition, enamel high-strength steel sheet of the present invention intensity with higher, good
Plasticity and weldability, particularly suitable for the high glass-lined equipment and accessory of the production confrontation quick-fried performance requirement of squama.
The manufacturing method of enamel high-strength steel sheet of the present invention with excellent two-sided application of slip performance equally has
There are above-mentioned advantages and beneficial effects.In addition to this, the manufacturing approach craft process is simple, does not need excessively to add valuable conjunction
Gold saves manufacturing cost.
Detailed description of the invention
Fig. 1 is microcosmic group of the enamel high-strength steel sheet with excellent two-sided application of slip performance of the embodiment of the present invention 1
Knit figure.
Fig. 2 is shown in the enamel high-strength steel sheet with excellent two-sided application of slip performance of the embodiment of the present invention 1
The small hole that TiN particle and periphery are formed.
Specific embodiment
Below in conjunction with Detailed description of the invention and specific embodiment to of the present invention with excellent two-sided application of slip performance
Enamel is made further explanation with high-strength steel sheet and its manufacturing method, however the explanation and illustration is not to this hair
Bright technical solution constitutes improper restriction.
Embodiment 1-7
Enamel high-strength steel sheet in above-described embodiment is made using following step:
(1) smelt and cast: smelting steel uses 300t top and bottom combined blown converter, and molten steel is through continuous casting machine casting at slab；
(2) hot rolling: the heating temperature before slab rolling is 1150~1250 DEG C, soaking time=t × (0.5~1.5),
Middle t is slab thickness, and unit mm, the unit of soaking time is min；1100~1200 DEG C of roughing rolling temperature of control, deformation
Amount >=50%；Water-spraying control after roughing, control finish rolling start rolling temperature are 920~1000 DEG C, and finishing temperature is 870~920 DEG C,
Deflection >=60%；
(3) cooling: to control average cooling rate≤10 DEG C/s.The type of cooling can use water-spraying control or slow cooling.
In addition, it is necessary to which explanation, in other implementations, in order to further increase the performance of steel, can also wrap
Include step (4) normalizing.
Table 1 lists the percent mass proportioning of each chemical element of each embodiment enamel high-strength steel sheet.
Table 1. (wt%, surplus are Fe and the other impurities element other than P)
Table 2 lists the specific process parameter of the manufacturing method of embodiment.
Table 2
Every mechanical property is carried out with high intensity to the enamel obtained by the above method with excellent two-sided application of slip performance
Energy test and enamel performance test will test the correlation performance parameters measured and be listed in Table 3 below.Wherein, enamel performance
Test is tested using: the application of slip, and the import glaze and domestic glaze of we selected typical carry out respectively, two-sided complete package wet process painting
It wards off, using a ground coat enamel and twice and more than twice overglaze, firing process is according to the regulation of glaze, and firing temperature is 850~950
℃。
Table 3
From table 3 it can be seen that each embodiment steel plate of this case yield strength >=370MPa, tensile strength >=
506MPa, elongation >=32%, illustrate that each embodiment enamel high-strength steel sheet of this case has higher intensity and good
Tensile ductility.
With continued reference to table 3, as seen from Table 3, the enamel described in this case with excellent two-sided application of slip performance is with high-strength
A good anti-quick-fried performance of squama can be had with the two-sided application of slip, and without squama burst point by spending steel plate, and with the adherence of ground coat enamel height, it is especially suitable
It shares in manufacture glass-lined equipment and its accessory.
Fig. 1 shows the micro- of the enamel high-strength steel sheet with excellent two-sided application of slip performance of the embodiment of the present invention 1
See tissue.
From figure 1 it appears that its microstructure of the enamel of embodiment 1 high-strength steel sheet be ferritic structure and
The pearlitic structrure of minute quantity (less than 10%), the visible TiN particle in ferrite crystal grain.
Fig. 2 is shown in the enamel high-strength steel sheet with excellent two-sided application of slip performance of the embodiment of the present invention 1
The small hole that TiN particle and periphery are formed.
From figure 2 it can be seen that the microstructure of the enamel high-strength steel sheet of embodiment of this case 1 has the micro- of storage hydrogen
Small hole, since what is involved is hot rolled steel plates for the technical program, this illustrates that the small hole of these storage hydrogen adds through overheat
It will not disappear after work, therefore be irreversible.
It should be noted that the above list is only specific embodiments of the present invention, it is clear that the present invention is not limited to above real
Example is applied, there are many similar variations therewith.If those skilled in the art directly exported from present disclosure or
All deformations associated, are within the scope of protection of the invention.
Claims (12)
1. a kind of enamel high-strength steel sheet with excellent two-sided application of slip performance, which is characterized in that its chemical element quality
Percentage are as follows:
C:0.06~0.15%, Si:0.16~0.50%, Mn:0.6~2.0%, S:0.010~0.035%, Al:0.001~
0.05%, Ti:0.15~0.25%, N:0.0035~0.010%, Nb:0~0.10%, surplus is Fe and other are inevitable
Impurity；
The enamel use high-strength steel sheet microstructure have ferrite and the TiN particle as precipitated phase, the TiN
The surface of son is in plane, is formed with irreversible small hole between the TiN particle and surface ferrite crystal grain in curved surface.
2. enamel high-strength steel sheet as described in claim 1, which is characterized in that it meets 4.5 × 10-2≤1.5×S+
3.43×N≤8.5×10-2, wherein S and N respectively indicates the mass percent of corresponding element；The microstructure also has conduct
The TiS particle of precipitated phase, the TiS particle is spherical in shape, and the TiS particle is used to form irreversible small hole.
3. enamel high-strength steel sheet as claimed in claim 1 or 2, which is characterized in that it meets 0.20%≤Ti+ (48*
Nb/93)≤0.25%.
4. enamel high-strength steel sheet as described in claim 1, which is characterized in that its also contain Cu:0.01~0.10%,
At least one of Mo:0.005~0.10%, Cr:0.01~0.10% and Ni:0.01~0.10%.
5. enamel high-strength steel sheet as described in claim 1, which is characterized in that the TiN particle is in square or length
Cube.
6. enamel high-strength steel sheet as described in claim 1, which is characterized in that its microstructure is ferrite+pearly-lustre
The Phase Proportion of body or ferrite+cementite, medium pearlite or cementite is 0-10%.
7. enamel high-strength steel sheet as described in claim 1, which is characterized in that ferritic average crystal grain diameter is little
In 20 μm.
8. enamel high-strength steel sheet as described in claim 1, which is characterized in that its yield strength >=345MPa, tension
Intensity >=450MPa, elongation percentage >=26%.
9. the manufacturing method of the enamel high-strength steel sheet as described in any one of claim 1-8 successively includes step
It is rapid:
(1) it smelts and casts；
(2) hot rolling: the heating temperature before slab rolling is 1150~1250 DEG C, soaking time=t × (0.5~1.5), wherein t
For slab thickness, unit mm, the unit of soaking time is min；1100~1200 DEG C of roughing rolling temperature of control, deflection >=
50%；Water-spraying control after roughing, control finish rolling start rolling temperature are 920~1000 DEG C, and finishing temperature is 870~920 DEG C, deformation
Amount >=60%；
(3) cooling.
10. manufacturing method as claimed in claim 9, which is characterized in that in the step (3), control average cooling rate
≤10℃/s。
11. manufacturing method as claimed in claim 9, which is characterized in that further include step (4) normalizing.
12. manufacturing method as claimed in claim 11, which is characterized in that in the step (4), control normalizing temperature exists
930~980 DEG C.
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| CN112139699B (en) * | 2019-06-28 | 2022-06-28 | 宝山钢铁股份有限公司 | Welding wire with yield strength of 550MPa grade for enamel steel |
| CN113373385A (en) * | 2020-02-25 | 2021-09-10 | 宝山钢铁股份有限公司 | Steel for glass lining and manufacturing method thereof |
| CN111411305B (en) * | 2020-04-21 | 2021-09-14 | 五矿营口中板有限责任公司 | High-toughness high-Ti low-alloy steel with thick glass lining and good glass lining performance and manufacturing method thereof |
| CN115110000B (en) * | 2022-06-28 | 2024-01-19 | 马鞍山钢铁股份有限公司 | 330MPa grade cold-rolled enamel steel and production method thereof |
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