CN107964633A - A kind of tinning substrate of resistance to timeliness and its manufacture method - Google Patents
A kind of tinning substrate of resistance to timeliness and its manufacture method Download PDFInfo
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- CN107964633A CN107964633A CN201610908292.8A CN201610908292A CN107964633A CN 107964633 A CN107964633 A CN 107964633A CN 201610908292 A CN201610908292 A CN 201610908292A CN 107964633 A CN107964633 A CN 107964633A
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- timeliness
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- 239000000758 substrate Substances 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 36
- 238000000034 method Methods 0.000 title claims abstract description 31
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 14
- 230000032683 aging Effects 0.000 claims abstract description 13
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 238000000137 annealing Methods 0.000 claims description 67
- 229910000831 Steel Inorganic materials 0.000 claims description 36
- 239000010959 steel Substances 0.000 claims description 36
- 238000005096 rolling process Methods 0.000 claims description 30
- 238000001816 cooling Methods 0.000 claims description 26
- 238000005097 cold rolling Methods 0.000 claims description 19
- 238000002791 soaking Methods 0.000 claims description 15
- 238000005098 hot rolling Methods 0.000 claims description 13
- 230000009467 reduction Effects 0.000 claims description 11
- 238000009749 continuous casting Methods 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 10
- 229910000859 α-Fe Inorganic materials 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 3
- 238000005554 pickling Methods 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 description 21
- 239000013078 crystal Substances 0.000 description 16
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 14
- 239000005028 tinplate Substances 0.000 description 14
- 238000001953 recrystallisation Methods 0.000 description 12
- 239000011572 manganese Substances 0.000 description 10
- 239000002245 particle Substances 0.000 description 9
- 230000008569 process Effects 0.000 description 9
- 229910000655 Killed steel Inorganic materials 0.000 description 7
- 238000005204 segregation Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 4
- 229910052796 boron Inorganic materials 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 230000003014 reinforcing effect Effects 0.000 description 4
- 210000001519 tissue Anatomy 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 230000008520 organization Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 229910017083 AlN Inorganic materials 0.000 description 2
- PIGFYZPCRLYGLF-UHFFFAOYSA-N Aluminum nitride Chemical compound [Al]#N PIGFYZPCRLYGLF-UHFFFAOYSA-N 0.000 description 2
- 206010068052 Mosaicism Diseases 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- TWHBEKGYWPPYQL-UHFFFAOYSA-N aluminium carbide Chemical compound [C-4].[C-4].[C-4].[Al+3].[Al+3].[Al+3].[Al+3] TWHBEKGYWPPYQL-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000004886 process control Methods 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 210000003765 sex chromosome Anatomy 0.000 description 2
- 239000007779 soft material Substances 0.000 description 2
- 238000003860 storage Methods 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 206010020880 Hypertrophy Diseases 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910001096 P alloy Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 238000007550 Rockwell hardness test Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000003712 anti-aging effect Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 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
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 235000013399 edible fruits Nutrition 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 230000002068 genetic effect Effects 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000004806 packaging method and process Methods 0.000 description 1
- 230000032696 parturition Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000033764 rhythmic process Effects 0.000 description 1
- 238000010079 rubber tapping Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
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- 238000006467 substitution reaction Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
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- 238000012795 verification Methods 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
- C21D1/26—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
- 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
-
- 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
- C22C38/002—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
- C22C38/02—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
- C22C38/06—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
- C22C38/14—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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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 Sheet Steel (AREA)
Abstract
The present invention relates to a kind of tinning substrate of resistance to timeliness and its manufacture method, and solving hardness number in the prior art can low, template, the technical problem of surface quality difference for the ageing resistance of 57 ± 3HR30Tm tinning substrates.A kind of tinning substrate of resistance to timeliness of the present invention, C≤0.005%, Si≤0.04%, Mn：0.3%~0.5%, P：0.05%~0.08%, S≤0.02%, Alt：0.01%~0.06%, N≤0.005%, Ti：0.04%~0.08%, surplus is iron and is unavoidably mingled with, the yield strength R of tinning substrateP0.2For 260~330MPa, yield tensile ratio 0.7~0.8, elongation after fracture A50For 35~45%, aging index AI values are 0~15MPa.Present invention is mainly used for the complicated can of effective requirement or deformation, the substrate of lid.
Description
Technical field
The present invention relates to a kind of cold rolling tinning substrate, more particularly to a kind of tinning substrate of resistance to timeliness and its manufacture method, tool
It is related to the tinning substrate of resistance to timeliness and its manufacture method that a kind of hardness number is 57 ± 3HR30Tm for body, the resistance to timeliness plating tinbase
Plate is produced with continuous annealing mode, is mainly used for the complicated can of effective requirement or deformation, the substrate of lid, is belonged to iron-based
Technical field of alloy.
Background technology
Tin plate is widely used in packaging industry with its excellent formability, corrosion resistance and decorative surface, wherein
Hardness HR30Tm is mainly used for some intensity there are certain requirements in 57 ± 3 soft material, while effective requirement or processing again
The production of complicated tank, lid is deformed, and the Main Mechanical of such product is all determined by the performance of plating prebasal plate substantially.
In the prior art, soft tin plate or tinning substrate component system generally uses carbon aluminium-killed steel or Ultra-low carbon
Steel, annealing way are generally produced using bell-type annealing or continuous annealing.Chinese patent document CN1888113A, hardness HR30Tm exist
Soft tin plate and its manufacture method in 51 ± 3, disclose a kind of by Ti-IF steel replacement Japan Ni-IF steel production hardness
HR30Tm is the production method of 51 ± 3 tin plate (MR T-1.5CA)；Chinese patent document CN1888114A, soft tin plate
And its manufacture method, disclose one kind and use Ti-IF steel to produce hardness HR30Tm as 49 ± 3 (MRT-1CA) and hardness HR30Tm
For the production method of 53 ± 3 (MRT-2CA) tin plates；Chinese patent document CN101643828A, a kind of anti-aging tinning black plate
Production method, disclose it is a kind of use carbon aluminium-killed steel perhydro bell-type annealing produce hardness HR30Tm for 55 ± 4 it is tin plating
The method of substrate；Chinese patent document CN101864534A, a kind of soft tin plate produced with continuous annealing mode, discloses one kind
Use methods of the carbon aluminium-killed steel continuous annealing mode production hardness HR30Tm for 55 ± 4 tin plate.
Tin plate disclosed in above-mentioned patent document and uncoated tinplate base are the product of IF steel bodies system, hardness number be all 51 ±
The soft material of below 3HR30Tm, and the tinning substrate that hardness number is 55 ± 4HR30Tm, substantially using carbon aluminium-killed steel
Continuous annealing or bell-type annealing production；Although bell-type annealing can partly solve the timeliness sex chromosome mosaicism of product, limited by its technique
System, the uniformity and surface quality of properties of product, template etc. are all less desirable, and use continuous annealing mode, due to annealing
Limited time, C, N atom in common carbon aluminium-killed steel have little time to separate out in the form of aluminium nitride and carbide, Wu Fashi
The requirement of existing product aging resistance.In fact, according to the standard hardness scope of tin plate it can be found that MR T-3 tin-plated products
Hardness number is 57 ± 3HR30Tm, exactly because the substrate that hardness number is 55 ± 4HR30Tm is considered in follow-up tin plating softening-melting process
The middle artificial aging that can occur 200 DEG C or so, hardness average can rise 2 or so, and therefore, the hardness range of substrate will be lower slightly
In finished product tin plate, this is exactly the carbon aluminium-killed steel production inevitable timeliness sex expression of T3 substrates.
In addition, some high-strength galvanizing plates are also designed using Ultra-low carbon, but since most of zinc-plated producing line is using horizontal continuous
Annealing furnace, its producing line total length is short compared with vertical continuous annealing furnace, this also means that its high temperature soak segment length is short, soaking time
Short, recrystallization annealing temperature is typically necessary more than 800 DEG C.
The content of the invention
The object of the present invention is to provide a kind of tinning substrate of resistance to timeliness and its manufacture method, solves hardness number in the prior art
For 57 ± 3HR30Tm tinning substrates ageing resistance can low, template, surface quality difference technical problem.
The technical solution adopted by the present invention is a kind of tinning substrate of resistance to timeliness, its chemical component weight percentage is：C≤
0.005%, Si≤0.04%, Mn：0.3%~0.5%, P：0.05%~0.08%, S≤0.02%, Alt：0.01%~
0.06%, N≤0.005%, Ti：0.04%~0.08%, surplus is iron and is unavoidably mingled with.
The metallographic structure of the tinning substrate of resistance to timeliness of the invention is ferrite, and tissue grain size number is I7.0~I8.5 grades,
The yield strength R of 0.25~0.50mm thickness tinning substratesP0.2 it is 260~330MPa, tensile strength RmFor 380MPa~430MPa,
Yield tensile ratio 0.7~0.8, elongation after fracture A50For 35~45%, hardness number is 57 ± 3HR30Tm, aging index AI values for 0~
15MPa。
The tinning substrate of resistance to timeliness of the invention is used for the complicated can of effective requirement or deformation, the substrate of lid.
The reasons why chemical composition of the tinning substrate of resistance to timeliness of the present invention limits within the above range is as follows：
C、N：Ensure the good ageing resistance of tinning substrate, seek to reduce C, the N content of the solid solution of steel intermediate gap as far as possible,
The tinning substrate of resistance to timeliness of the invention is produced using continuous annealing process, but in continuous annealing producing line, since annealing time is limited,
C, N atom in common carbon aluminium-killed steel has little time to separate out in the form of aluminium nitride and carbide still to be deposited with free state
It can not realize the requirement of product ageing resistance, therefore, the present invention takes Ultra-low carbon, the composition design of nitrogen, fundamentally solves
The problem of free C, N, meet product ageing resistance requirement.Therefore, the present invention limits C≤0.005%, N≤0.005%.
Si：Si has certain reinforcing effect, but influences surface quality, since the present invention is tinning substrate, Surface Quality
It is more demanding, therefore take low silicon to design, set Si≤0.04%.
Mn：Mn is deoxidier and desulfurizing agent generally in steel, eliminates or reduce the red brittleness as caused by S.Meanwhile manganese is also
A kind of intensified element, it forms solid solution with iron, can improve ferritic hardness and strength in substrate tissue.But Mn contents are not yet
Can be excessive, on the one hand excessive Mn can make the mouldability of product be affected, on the other hand due to column easily in the operation of rolling
It is brilliant substantially to cause rolling crack.Consider the aimed hardness value of the present invention and the realizability of production, what the present invention was set
Mn contents are 0.3%~0.5%.
P:Since easily segregation causes cold short in steel, P is harmful element generally in steel, but at the same time, P is also a kind of strong
Change element, the distortion of lattice dot matrix is caused with P existing for the solution of gap, hinder dislocation movement, improve intensity, meanwhile, P
Also intensity can be improved by postponing recrystallization softening ferrite crystal grain.In addition, the Secondary phase particle that the element such as P and Ti, Fe is formed exists
Matrix strength can also be improved by being separated out under certain annealing temperature.To give full play to the solid solution strengthening effect of P and the Secondary phase particle containing P
Precipitating reinforcing effect, while offset since Secondary phase particle separates out the consumption of the P brought, through theoretical calculation and experimental verification, this hair
The bright P content set is 0.05%~0.08%.
To avoid the segregation of P, many documents, which are all mentioned, can add micro boron, especially in bell-type annealing, when long
Between and slowly in cooling procedure, suppress the segregation of phosphorus using quick separate out of the boron element in crystal boundary.But since boron is at 900 DEG C
Recrystallization can be substantially postponed above, reduces the crystallite dimension of hot rolled plate, and this relatively small crystallite dimension is genetic to follow-up cold
Process is rolled, annealing temperature certainly will be further improved and can be only achieved required crystallite dimension and hardness range, therefore, synthesis is examined
Consider the reasonability of full process production cost and organization of production, the present invention does not add boron element.
In addition, the characteristics of present invention utilizes continuous annealing high speed in short-term, by rationally setting soaking zone temperature, soaking time
And cooling section speed, segregations of the P in crystal boundary is avoided or reduced by the control of crystallite dimension, reduces the adverse effect of P.
S：S is in the present invention harmful element, and content is as low as possible, but considers the cost and its capability of influence of desulfurization,
Present invention setting S≤0.02%.
Al：Al is also a kind of nitride forming element, can fix nomadic nitrogen in steel, improves ageing resistance, but its content
Can not be excessive, it otherwise can form excessive deoxidation products Al2O3It is mingled with.The Al content that the present invention limits is 0.01%~0.06%.
Ti：Ti is the formation element of common carbon, nitride in IF steel, primarily serves fixed free C, N, it is resistance to improve product
The effect of timeliness.Its content lower limit is mainly determined by the content of C, N in steel, simultaneously as Ti can improve recrystallization annealing temperature
Degree, therefore, its content can not be excessive.The Ti contents set with reference to C, N content and the follow-up annealing process of the present invention, the present invention
For 0.04%~0.08%.
A kind of manufacture method for the tinning substrate of resistance to timeliness, this method include：
Molten steel obtains continuous casting steel billet through continuous casting, wherein the percentage by weight of the ladle chemistry is：C≤0.005%,
Si≤0.04%, Mn：0.3%~0.5%, P：0.05%~0.08%, S≤0.02%, Alt：0.01%~0.06%, N≤
0.005%, Ti：0.04%~0.08%, surplus is Fe and inevitable impurity element；
Continuous casting steel billet carries out hot rolling, the hot rolling is rolled for two-part in 1180~1220 DEG C after heating 180~240min
Technique processed, roughing are 5 passage tandem rollings, and finish rolling is 7 passage tandem rollings, and finish rolling end temp is 890~930 DEG C；Steel plate is thick after finish rolling
Spend and cooled down for 2.0~3.5mm, section cooling using leading portion, coiling temperature batches acquisition coils of hot-rolled steel for 660~700 DEG C；
Coils of hot-rolled steel is again 0.25mm through pickling, cold rolling, vertical continuous annealing furnace annealing, the smooth thickness that obtains after uncoiling
~0.50mm finished product tinning substrates, the cold rolling reduction ratio are 82%~90%, roll hard state strip vertical after cold rolling
The soaking zone temperature of formula continuous annealing furnace annealing is 680 DEG C~720 DEG C, and strip is 60s~95s in the annealing time of soaking zone；
Through quick cooling, strip cooling velocity be 30~50 DEG C/s for strip after annealing, strip the temperature of rapid cooling terminal be 300 DEG C~
350℃；It is smooth to extend to rate 1.5~2.5%.
The reasons why production technology that the present invention takes, is as follows：
1st, the setting of continuous casting steel billet heating-up temperature and heating time
The setting of continuous casting steel billet acid extraction is mainly that guarantee reaches finishing temperature requirement, in addition, also needing to consider
The surface quality of slab, tapping temperature is higher, and scale on surface is more serious.The present invention is designed using Ultra-low carbon, usual Ar3Line
At 880~900 DEG C or so, to avoid hot fine rolling at the end of temperature is too low enters the rolling of austenite and ferritic two-phase section and produce
Raw mixed crystal, considers normal temperature drop during hot rolling, and the present invention sets continuous casting steel billet heating-up temperature as 1180~1220 DEG C.Heating
The main actual temperature considered when slab enters heating furnace of setting of time has differences, to realize temperature inside and outside final slab of coming out of the stove
Degree is uniform, meanwhile, the organization of production rhythm and energy consumption cost of consideration hot rolling actual production, general heating time are set as 180
~240min.
2nd, finish rolling end temp is set
Finish rolling end temp principal security finish rolling rolling completes (Ar in austenitic area3It is more than line), the present invention is using ultralow
Carbon designs, usual Ar3Line is at 880~900 DEG C or so, and the addition of P element is further by Ar3Line improves 10 DEG C or so, but together
When, finish rolling end temp also can not be excessive, and being otherwise also easy to produce substantial amounts of iron scale influences surface quality, therefore, binding test
With live trial manufacture experience, finish rolling end temp is set as 890~930 DEG C.
3rd, after finish rolling section cooling mode setting
The main requirement for considering smart cooling velocity after rolling of the selection of section cooling mode, due to smart in the application
It is higher to roll end temp, if cooling velocity is too slow, it will cause actual temperature of the steel plate in follow-up curling to be higher than
Setting value, crystal grain grows excessively thick in annealing process, this Structure Inheritance to cold rolling, it will it is hard to influence finished strip target
The realization of degree.Therefore, section cooling mode selects the faster leading portion cooling of cooling rate after finish rolling.
4th, hot-rolling coiling temperature is set
The analysis of the main size and carbon, nitride and Secondary phase particle for considering ferrite crystal grain of setting of hot rolling coiling temperature
Go out.In general, the coiling temperature of ultra-low-carbon steel is higher, ferrite crystal grain is bigger, while the size that Secondary phase particle separates out also is got over
Greatly.The present invention combines follow-up annealing process requirement, considers, sets hot-rolling coiling temperature as 660 DEG C~700 DEG C.
5th, cold rolling reduction ratio is set
The setting of cold rolling reduction ratio is main to be considered to be crushed the reply power of elongated grain annealing recrystallization.It is general and
Speech, with the raising of reduction ratio, its internal dislocation density also significantly improves, and it can be largely with dislocation to recrystallize storage
Form stores, and therefore, reduction ratio is higher, and the driving force of recrystallization is also bigger, while also recrystallization annealing temperature can be made to have one
Determine the decline of degree.But reduction ratio is also impossible to too greatly, and this aspect is limited by capacity of equipment, on the other hand more than a certain range
Reduction ratio, its influence to recrystallization gradually weakens, and therefore, the present invention gropes by test of many times and practice, preferable cold
Reduction ratio is rolled for 82~90%.
6th, the setting of annealing temperature and annealing time
The present invention using vertical continuous oven to roll it is hard after strip carry out continuous annealing, annealing temperature and soaking time are set
It is fixed mainly to roll the recovery and recrystallization state of hard state strip and the precipitation quantity and size of Secondary phase particle in order to control, in addition,
Annealing temperature setting also needs to consider Warm status and production cost of the strip in stove, avoids the excessive incident wooden dipper of temperature bent disconnected
The production and Transition Materials cost that band and temperature additionally occur when switching.The present invention is through groping, and annealing temperature is at 680 DEG C~720 DEG C
When, back dissolving is more tiny Secondary phase particle to Ti, P Secondary phase particle that hot rolled plate separates out again, prevents growing up for recrystal grain,
Improve hardness.In addition, in the temperature range and the soaking time of 60s~95s, strip is basically completed recrystallization, grain size I7.0
~I8.5 grades, hardness reaches target call.If annealing temperature does not reach the scope, the longer recrystallization time is on the one hand needed,
Speed of production, production capacity and cost are influenced, is on the other hand lost due to fast heating at high temperature, it is equal that nucleation rate significantly improves rear crystal grain
The effect of even and fineization.If annealing temperature is higher than this temperature, though it can accelerate to recrystallize, in identical soaking time, continuous annealing speed
Under, on the one hand can promote crystal grain hypertrophy, hardness is difficult to reach target call, reduce the reinforcing effect of Ti, P alloy, it is necessary to
Further shorten soaking time, improve continuous annealing speed, this can undoubtedly bring the risk of unit capacity and production stability；Separately
One side temperature is excessive not to reach reinforcing target more than the optimal Precipitation Temperature scope of Secondary phase particle.Therefore, through repeatedly exploring, this hair
The bright annealing temperature for setting strip in vertical continuous annealing furnace soaking zone is set as 680 DEG C~720 DEG C in the annealing time of soaking zone
It is set to 60s~95s.
7th, the setting of the cooling velocity and rapid cooling outlet temperature of strip after annealing
For strip after annealing through quick cooling, the setting of cooling velocity is mainly the segregation to reduce P element in crystal boundary, drop
The adverse effect of low P element.Through research, the Grain Boundary Character of ultra-low-carbon steel is distributed, crystallite dimension closely related with its crystallite dimension
It is smaller, more easily there is low energy crystal boundary around it, and since the atomic arrangement on low energy crystal boundary is more neat, so that solute is former
Sub- P is not easy segregation.Therefore, ferrite grain size is influenced by controlling cooling velocity, can preferably reduces P element
Segregation.Through considering the practical capacity of vertical continuous annealing furnace, the strip after present invention setting annealing is in rapid chilling section
Cooling velocity is 30~50 DEG C/s, and strip is 300 DEG C~350 DEG C in the temperature of rapid cooling terminal.
8th, smooth elongation percentage setting
The present invention is smooth to strip progress using Two-stand Temper Mill, and when smooth elongation control is less than 1.5%, surrender is flat
Platform is difficult to eliminate, and plate shape and surface roughness can not ensure；When smooth elongation percentage is higher than 2.5%, hardness and strength will be notable
Improve, the deterioration of material processability.Therefore, the present invention sets smooth elongation percentage as within 1.5~2.5%.
The metallographic structure of the tinning substrate of resistance to timeliness of the method for the present invention production is used as ferrite, tissue grain size number is
I7.0~I8.5 grades, the yield strength R of 0.25~0.50mm thickness tinning substratesP0.2For 260~330MPa, tensile strength RmFor
380MPa~430MPa, yield tensile ratio 0.7~0.8, elongation after fracture A50For 35~45%, hardness number is 57 ± 3HR30Tm, timeliness
Index A I values are 0~15MPa.
The present invention has following good effect compared with prior art：1st, tinning substrate of the present invention is set by using Ultra-low carbon
Meter, product timeliness sex chromosome mosaicism caused by solving free C, N element from root, aging index are less than 15MPa.2nd, the present invention is logical
The intensified element such as P, Mn, Ti component and corresponding hot rolling, the reasonable combination of cold-rolling process are crossed, except successfully realizing case hardness
HR30Tm is outside 57 ± 3 target call, yield strength, the yield tensile ratio of product can meet tin plate be packed for it is complicated it is molding will
The problems such as asking, overcoming existing easy to crack, barring during the complicated shaping of existing tinning substrate.3rd, the method for the present invention is used and continuously moved back
Ignition technique produces, and avoids the quality such as bell-type annealing production cold-reduced sheet surface quality is bad, performance uniformity is poor, template is bad and asks
Topic.4th, due to ultra-low-carbon steel is elongated after cold rolling crystal grain during recovery and recrystallization preferentially giving birth to there are different orientation crystal grain
Growth process, the higher annealing temperature of relatively conventional ultra-low-carbon steel, the method for the present invention use 700 DEG C or so relatively low of annealing
Temperature, { 111 } favourable to mouldability orientation crystal grain preferred growth, the grain growth of other orientations is slow or suppressed, finally
Grain structure is in pie crystal grain mostly；The dosage of Transition Materials and the time of heating and cooling are reduced, improves production efficiency, reduction is produced into
This, and the risk that broken belt occurs in stove is reduced, organization of production is convenient.
Brief description of the drawings
Fig. 1 is the metallographic structure photo of the tinning substrate of resistance to timeliness embodiment 2 of the invention.
Embodiment
With reference to embodiment 1~3, the present invention will be further described.
Table 1 is the chemical composition (by weight percentage) of steel of the embodiment of the present invention, and surplus is iron and inevitable impurity.
The chemical composition of 1 steel of the embodiment of the present invention of table, unit：Percentage by weight.
| Element | C | Si | Mn | P | S | Alt | N | Ti |
| The present invention | ≤0.005 | ≤0.04 | 0.3-0.5 | 0.05-0.08 | ≤0.02 | 0.01-0.06 | ≤0.005 | 0.04-0.08 |
| Embodiment 1 | 0.0026 | 0.025 | 0.42 | 0.074 | 0.01 | 0.03 | 0.0035 | 0.046 |
| Embodiment 2 | 0.0015 | 0.028 | 0.33 | 0.066 | 0.012 | 0.035 | 0.0042 | 0.06 |
| Embodiment 3 | 0.004 | 0.03 | 0.45 | 0.053 | 0.016 | 0.053 | 0.0025 | 0.055 |
Obtain meeting the requirements the molten steel of chemical composition by converter melting, and molten steel is connected after RH stove Fruit storages
Casting obtains continuous casting steel billet, and thickness is 210~230mm, and width is 800~1300mm, and length is 5000~10000mm.
The scale slab of STEELMAKING PRODUCTION send to heating furnace and reheats, and is sent after dephosphorization of coming out of the stove to rolling on continuous hot tandem rolling mill
System.After roughing milling train and finish rolling Continuous mill train controlled rolling, section cooling is cooled down using leading portion, is then batched, and is produced
Go out coils of hot-rolled steel.Hot rolling technology control is shown in Table 2.
2 hot rolling technology control parameter of the embodiment of the present invention of table
| Hot Rolling Parameters | Slab heating temperature/DEG C | Finish rolling end temp/DEG C | Coiling temperature/DEG C | Hot rolled steel plate thickness/mm |
| The present invention | 1180-1220 | 890-930 | 660-700 | 2.0-3.5 |
| Embodiment 1 | 1195 | 913 | 685 | 2.0 |
| Embodiment 2 | 1210 | 925 | 696 | 3.5 |
| Embodiment 3 | 1183 | 899 | 668 | 3.2 |
By above-mentioned coils of hot-rolled steel again uncoiling after overpickling, in 6 roller UCM (omnipotent convexity band intermediate calender rolls play) 5 racks
Cold continuous rolling carries out once cold rolling, and the reduction ratio of cold rolling is 82%~90%, and the strip of hard state is rolled after cold rolling by vertical
Formula continuous annealing furnace annealing, the smooth finished product tinning substrate for obtaining 0.25~0.50mm of thickness.Annealing process is：Strip is vertical
The annealing temperature of the soaking zone of continuous annealing furnace is 680 DEG C~720 DEG C, is 60s~95s in the annealing time of soaking zone.Cold rolling,
Annealing, flattening process control parameter are shown in Table 3.
3 cold rolling of the embodiment of the present invention of table, annealing, flattening process control parameter
The tinning substrate of resistance to timeliness obtained using the above method, referring to Fig. 1, the metallographic structure for the tinning substrate of resistance to timeliness is iron
Ferritic, tissue grain size number are I7.0~I8.5 grades, the yield strength R of 0.25~0.50mm thickness tinning substratesP0.2For 260~
330MPa, tensile strength RmFor 380MPa~430MPa, yield tensile ratio 0.7~0.8, elongation after fracture A50For 35~45%, hardness
It is 0~15MPa to be worth for 57 ± 3HR30Tm, aging index AI values.
By the obtained cold rolling tin plate of the present invention according to《GB/T228.1-2010 metal material stretching test part 1s：
Room temperature test method》Tension test is carried out, according to metal material Rockwell hardness test part 1：Test method (GB/T230.1-
2009) hardness test is carried out.The mechanical property of steel plate is shown in Table 4.
The mechanical property of 4 cold rolling tin plate of the embodiment of the present invention of table
In addition to the implementation, the present invention can also have other embodiment.It is all to use equivalent substitution or equivalent transformation shape
Into technical solution, all fall within the protection domains of application claims.
Claims (3)
1. a kind of thickness is 0.25~0.50mm tinning substrates of resistance to timeliness, its chemical component weight percentage is：C≤0.005%,
Si≤0.04%, Mn：0.3%~0.5%, P：0.05%~0.08%, S≤0.02%, Alt：0.01%~0.06%, N≤
0.005%, Ti：0.04%~0.08%, surplus is iron and is unavoidably mingled with；The metallographic structure of the tinning substrate of resistance to timeliness
For ferrite, the tissue grain size number is I7.0~I8.5 grades, the yield strength R for the tinning substrate of resistance to timelinessP0.2For 260~
330MPa, tensile strength RmFor 380MPa~430MPa, yield tensile ratio 0.7~0.8, elongation after fracture A50For 35~45%, hardness
It is 0~15MPa to be worth for 57 ± 3HR30Tm, aging index AI values.
2. a kind of manufacture method for the tinning substrate of resistance to timeliness, including：
Molten steel obtains continuous casting steel billet through continuous casting, wherein the percentage by weight of the ladle chemistry is：C≤0.005%, Si≤
0.04%, Mn：0.3%~0.5%, P：0.05%~0.08%, S≤0.02%, Alt：0.01%~0.06%, N≤
0.005%, Ti：0.04%~0.08%, surplus is Fe and inevitable impurity element；
Continuous casting steel billet carries out hot rolling, the hot rolling rolls work for two-part in 1180~1220 DEG C after heating 180~240min
Skill, roughing are 5 passage tandem rollings, and finish rolling is 7 passage tandem rollings, and finish rolling end temp is 890~930 DEG C；Section cooling is adopted after finish rolling
Cooled down with leading portion, coiling temperature batches acquisition coils of hot-rolled steel for 660~700 DEG C；
Coils of hot-rolled steel again after uncoiling through pickling, cold rolling, vertical continuous annealing furnace annealing, it is smooth obtain thickness for 0.25mm~
0.50mm finished product tinning substrates, the cold rolling reduction ratio are 82%~90%, roll hard state strip vertical after cold rolling
The soaking zone temperature of continuous annealing furnace annealing is 680 DEG C~720 DEG C, and strip is 60s~95s in the annealing time of soaking zone；Move back
Through quick cooling, strip cooling velocity be 30~50 DEG C/s for strip after fire, strip the temperature of rapid cooling terminal be 300 DEG C~
350℃；It is smooth to extend to rate 1.5~2.5%.
3. the manufacture method of the tinning substrate of resistance to timeliness as claimed in claim 2, it is characterized in that, after hot fine rolling, control hot rolling
Steel plate thickness is 2.0~3.5mm.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN108998723A (en) * | 2018-06-14 | 2018-12-14 | 河钢股份有限公司 | A kind of high temperature resistant accelerated ag(e)ing steel plate and its production method |
| CN109136777A (en) * | 2018-08-03 | 2019-01-04 | 首钢集团有限公司 | A kind of secondary cold-rolling tin plate and its production method |
| CN109136780A (en) * | 2018-09-26 | 2019-01-04 | 首钢集团有限公司 | A kind of aerosol top ends of cans tin plate and its production method |
| CN111549285A (en) * | 2020-06-18 | 2020-08-18 | 武汉钢铁有限公司 | Ultra-low carbon tin plate with excellent corrosion resistance and preparation method thereof |
| CN111621704A (en) * | 2020-06-17 | 2020-09-04 | 武汉钢铁有限公司 | Boron and chromium-containing ultra-low carbon tin plate with hardness HR30Tm within 55 +/-4 and manufacturing method thereof |
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| CN104946978A (en) * | 2015-07-07 | 2015-09-30 | 新余钢铁集团有限公司 | Color-coated cold-rolled baseplate used for household appliance panel and manufacturing method of color-coated cold-rolled baseplate |
| CN105112776A (en) * | 2015-08-25 | 2015-12-02 | 上海梅山钢铁股份有限公司 | Phosphorus-containing low-carbon cold-rolled hard tin-plated steel plate and production method thereof |
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| CN1888113A (en) * | 2005-06-29 | 2007-01-03 | 宝山钢铁股份有限公司 | Soft tin-plate of hardness HR30T 51+/-3 and its making process |
| CN104946978A (en) * | 2015-07-07 | 2015-09-30 | 新余钢铁集团有限公司 | Color-coated cold-rolled baseplate used for household appliance panel and manufacturing method of color-coated cold-rolled baseplate |
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| CN108998723A (en) * | 2018-06-14 | 2018-12-14 | 河钢股份有限公司 | A kind of high temperature resistant accelerated ag(e)ing steel plate and its production method |
| CN109136777A (en) * | 2018-08-03 | 2019-01-04 | 首钢集团有限公司 | A kind of secondary cold-rolling tin plate and its production method |
| CN109136780A (en) * | 2018-09-26 | 2019-01-04 | 首钢集团有限公司 | A kind of aerosol top ends of cans tin plate and its production method |
| CN111621704A (en) * | 2020-06-17 | 2020-09-04 | 武汉钢铁有限公司 | Boron and chromium-containing ultra-low carbon tin plate with hardness HR30Tm within 55 +/-4 and manufacturing method thereof |
| CN111748747A (en) * | 2020-06-17 | 2020-10-09 | 武汉钢铁有限公司 | Ultralow-silicon ultralow-aluminum semi-boiling steel and smelting method |
| CN111549285A (en) * | 2020-06-18 | 2020-08-18 | 武汉钢铁有限公司 | Ultra-low carbon tin plate with excellent corrosion resistance and preparation method thereof |
| CN114214562A (en) * | 2021-12-03 | 2022-03-22 | 首钢集团有限公司 | A kind of soft tinplate, preparation method and container |
| CN115341155A (en) * | 2022-10-17 | 2022-11-15 | 江苏省沙钢钢铁研究院有限公司 | A kind of tinplate and its manufacturing method |
| CN115341155B (en) * | 2022-10-17 | 2023-02-24 | 江苏省沙钢钢铁研究院有限公司 | Tin plate and manufacturing method thereof |
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