CN102325608B - Hot rolled thin cast steel strip product and manufacture method thereof - Google Patents
Hot rolled thin cast steel strip product and manufacture method thereof Download PDFInfo
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- CN102325608B CN102325608B CN201080008606.XA CN201080008606A CN102325608B CN 102325608 B CN102325608 B CN 102325608B CN 201080008606 A CN201080008606 A CN 201080008606A CN 102325608 B CN102325608 B CN 102325608B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
Abstract
The invention provides a kind of hot rolled strip, it is by comprising the following steps to manufacture: assembling double-roller continuous casting machine, form the casting molten bath of molten steel, described molten steel there is the free oxygen content of 20 ~ 75ppm and its composition makes cast steel strip comprise be less than 0.25 % by weight carbon, the manganese of 0.9 ~ 2.0 % by weight, the silicon of 0.05 ~ 0.50 % by weight, be greater than 0.01 % by weight and be less than or equal to the phosphorus of 0.15 % by weight and be less than the aluminium of 0.01 % by weight, reversely rotate dynamic casting roll and form steel band, steel band described in hot rolling makes mechanical performance when drafts is 10% and 35% in yield strength, the difference in change of tensile strength and general extension aspect is within 10%, and batch steel band to provide the most microstructure containing bainite and acicular ferrite the temperature of 300 ~ 700 DEG C.Alternatively, described steel can comprise the copper of 0.20 ~ 0.60% and be low to moderate the manganese of 0.08%.
Description
Background and general introduction
In double-roll type conticaster (twinrollcaster), make metal shells solidify on the roll surface of movement between inner-cooled casting roll motlten metal being introduced a pair reverse rotation, and being produced by the roll gap brought into together between casting roll the band product solidified, this band product transmits downwards from the roll gap between casting roll.Term used herein " roll gap " refers to casting roll near general area (generalregion) together.Motlten metal pours into through metal transfer system from ladle (ladle) to form the casting molten bath of motlten metal, wherein this metal transfer system comprises tundish and is positioned at core-inset type nozzle (corenozzle) above roll gap, and the length on the casting surface that this casting molten bath is supported on the roller be positioned at above roll gap and along roll gap extends.Between the infusibility side plate that this casting molten bath is limited in usually and the end surface of roller is arranged in sliding manner or baffle plate (dam), thus two ends blocking casting molten bath prevent from flowing out.Cast steel strip (caststrip) is guided into usually to hot-rolling mill, and in this hot-rolling mill, this steel band is by under hot pressing 10% or more.
In the past, on double-roll type conticaster, cast common (plain) mild steel continuously, comprised common carbon/manganese steel.The impact of (hotrollingreduction) under the hot rolling that the physical property of these common carbon/manganese steel generally can be increased.Such as, along with the increase of hot rolling amount, yield strength and tensile strength reduce, and along with the increase of hot rolling amount, general extension generally can increase.Therefore, in the past, must regulate to provide required mechanical performance for the applied composition of hot rolling drafts to steel.This will cause inefficiency and operational issue, because steelshop must provide different meltings to form for different hot rolled strip thickness to provide required hot-rolled steel performance.
In addition, the composition of steel can comprise the copper from the waste be mixed in molten steel.Past, generally avoid the copper concentration being greater than about 0.2 % by weight, this is because " red brittleness (hotshortness) " under considering hot rolling in process, this can cause crack or very coarse surface appear in steel band (strip), is sometimes called " checking (checking) ".When copper concentration is greater than in the situation of 0.2% (such as in the steel of against weather with improvement), expensive additive such as nickel must be added to reduce hot short risk.
Hot short problem has added and has used electric arc furnaces to form the cost of molten carbon steel in manufacture low-alloy steel.Being manufactured about 75% in the cost of steel by electric arc furnaces is be used as to the cost of the steel scrap of the raw material of electric-arc furance loading (scrap).According to copper content steel waste material is divided into that copper content is less than 0.15 % by weight, copper content is more than or equal to 0.15 % by weight and is greater than 0.5 % by weight to as high as 0.5 % by weight and copper content traditionally.Copper content be greater than 0.5% steel scrap can the low steel scrap of mixed copper concentration to manufacture available steel scrap.In any case the steel scrap that copper content is less than 0.15 % by weight is the steel scrap of most worthy, and the value of the steel scrap of other two kinds of grades is then less.The steel scrap that copper content is less than 0.15 % by weight is generally used for the industrially preparing process for some steel in electric arc furnaces, considerably increases the cost of generated steel plate.Copper content up to 0.5% steel scrap grade for use electric arc furnaces bar milk in or in process for other, in other process described, the steel scrap lower with copper content mixes and is less than 0.15% cost a lot of money to be decreased to by total copper content of steel scrap.
The invention discloses a kind of hot rolled strip and manufacture method thereof, it comprises the following steps:
(a) assembling inner cooling type roller conticaster, it has the casting roll being positioned at side, between casting roll, form roll gap,
B () forms the casting molten bath of molten steel, described casting molten bath to be supported in the casting roll above roll gap and to be limited near casting roll end by side shield, described molten steel has the free oxygen content of 20 ~ 75ppm, its composition makes the composition of manufactured hot rolled thin cast steel strip (caststrip) comprise to be less than the carbon of 0.25 % by weight, be greater than 0.01 % by weight and be less than or equal to 0.15 % by weight phosphorus, 0.9 ~ 2.0 % by weight manganese, 0.05 ~ 0.50 % by weight and be less than 0.01 % by weight aluminium
C () reversely rotates described casting roll and to make when described casting roll moves through described casting molten bath solidify metal shells in casting roll, and
D () moves downward through described roll gap between casting roll to form steel band by described metal-back,
E steel band described in () hot rolling makes difference in change the 10% within (within10%foryieldstrength of mechanical performance in yield strength, tensile strength and general extension when drafts is 10% and 35%, tensilestrengthandtotalelaongation), and
F () batches hot rolled strip to provide the most microstructure containing bainite and acicular ferrite the temperature of 300 ~ 700 DEG C.
Alternatively, hot-rolled step can make the difference in change of mechanical performance when drafts is 15% and 35% in yield strength, tensile strength and general extension within 10%.In addition optionally, the difference in change of the mechanical performance in the gamut of 15% ~ 35% drafts in yield strength, tensile strength and general extension is within 10%.Alternatively, the difference in change of the mechanical performance in the gamut of 10% ~ 35% drafts in yield strength, tensile strength and general extension is within 10%.
The composition of molten steel can contain the free oxygen content of 30 ~ 60ppm.The total oxygen content of the motlten metal of hot rolled strip can be 70ppm ~ 150ppm.
The composition of molten steel makes the Fe content of the composition of hot rolled strip be 0.9 ~ 1.3 % by weight.
The composition of molten steel makes the composition of hot rolled strip can comprise the niobium of 0.01 % by weight ~ 0.20 % by weight in addition.Alternatively or extraly, molten steel can have certain composition and makes the composition of hot rolled strip comprise at least one to be in addition selected from following element: the molybdenum of about 0.05 % by weight ~ about 0.50 % by weight, the vanadium of about 0.01 % by weight ~ about 0.20 % by weight and their mixture.
Hot rolled strip can be provided as the coating with zinc or kirsite or aluminium extraly.Hot rolled strip is the yield strength also can after at least 35% with at least 440Mpa at hot rolling drafts.
The invention also discloses a kind of hot rolled strip and manufacture method thereof, it comprises the following steps:
(a) assembling inner cooling type roller conticaster, it has the casting roll being positioned at side, between casting roll, form roll gap,
B () forms the casting molten bath of molten steel, described casting molten bath to be supported in the casting roll above roll gap and to be limited near casting roll end by side shield, described molten steel has the free oxygen content of 20 ~ 75ppm, its composition makes the composition of described hot rolled strip comprise the carbon being less than 0.25 % by weight, the manganese of 0.2 ~ 2.0 % by weight, the silicon of 0.05 ~ 0.50 % by weight, be greater than 0.01 % by weight and be less than or equal to 0.15 % by weight phosphorus, be less than the tin of 0.03 % by weight, be less than the nickel of 0.20 % by weight, be less than the aluminium of 0.01 % by weight and the copper of 0.20 ~ 0.60 % by weight,
C () reversely rotates described casting roll and to make when described casting roll moves through described casting molten bath solidify metal shells in casting roll,
D () moves downward through described roll gap between casting roll to form steel band by described metal-back,
E steel band described in () hot rolling makes mechanical performance when drafts is 10% and 35% difference in change in yield strength, tensile strength and general extension within 10%, and
F () batches hot rolled strip to provide the most microstructure containing bainite and acicular ferrite the temperature of 300 ~ 700 DEG C.
Alternatively, hot-rolled step can make the difference in change of mechanical performance when drafts is 15% and 35% in yield strength, tensile strength and general extension within 10%.In addition optionally, the difference in change of the mechanical performance in the gamut of 15% ~ 35% drafts in yield strength, tensile strength and general extension is within 10%.Alternatively, the difference in change of the mechanical performance in the gamut of 10% ~ 35% drafts in yield strength, tensile strength and general extension is within 10%.
Molten steel can have the free oxygen content of 30 ~ 60ppm.The total oxygen content of the motlten metal of hot rolled strip can be 70ppm ~ 150ppm.Nickel content can be less than 0.1 % by weight.
Molten steel can have certain composition and make the copper content of the composition of hot rolled strip be 0.2 ~ 0.5 % by weight or 0.3 ~ 0.4 % by weight.The composition of molten steel can have certain composition in addition and make the composition of hot rolled strip additionally have the chromium content of 0.4 ~ 0.75 % by weight or 0.4 ~ 0.5 % by weight.
Brief description of drawings
With reference to accompanying drawing, the present invention is further described, wherein:
Fig. 1 shows the steel foundry equipment combining (in-line) hot-rolling mill and coiling machine continuously;
Fig. 2 shows the details of twin roll strip caster;
Fig. 3 shows the diagram of hot rolling drafts on the impact of the yield strength of potassium steel (elevatedmanganesesteel);
Fig. 4 shows the diagram of hot rolling drafts on the yield strength of 0.19% carbon steel and the impact of elongation;
Fig. 5 shows carbon amounts to the diagram containing the tensile strength (TS) of test sample book of manganese of 0.88% ~ 1.1%, the impact of yield strength (YS) and elongation (TE); And
Fig. 6 shows hot rolling drafts in the scope of about 15% ~ 45% drafts diagram on the impact of tensile strength, yield strength and elongation.
The detailed description of accompanying drawing
Fig. 1 shows the continuous member of the strip caster for continuous casting of steel band.Fig. 1 and 2 shows double-roller continuous casting machine 11, its continuous seepage casted steel belt 12, and casted steel belt 12 enters transfer path 10 and through guide table 13 to the stretch-draw roller tables 14 with pinch rolls 14A.After leaving stretch-draw roller tables 14, steel band enters in the hot-rolling mill 16 containing a pair reduction roll 16A and backing roll 16B immediately, and here cast steel strip carries out hot rolling to reduce the thickness wanted.Hot rolled strip is sent to runout table 17, in runout table 17 steel band by with the convection current of water with to contact and radiation cools, wherein said water is provided by water jet 18 (or other suitable means).Rolling with cooling steel band then through comprising a pair pinch rolls 20A stretch-draw roller tables 20 and be sent to coiling machine 19 afterwards.Final cooling casting steel band after batching.
As shown in Figure 2, double-roller continuous casting machine 11 comprises machine mainframe 21, and it supports the casting roll 22 with casting surface 22A being positioned at side for a pair.In casting operation process, motlten metal is provided in tundish 23 from ladle (not shown), through infusibility guard shield 24 to distributor or moveable tundish 25, and the transmission nozzle 26 then between the casting roll 22 of distributor 25 above roll gap 27.The motlten metal transmitted between casting roll 22 forms the casting molten bath 30 be positioned at above roll gap.The end that baffle plate or plate 28 are limited to casting roll is closed by an offside in casting molten bath 30, casting roll pushed to by baffle plate or plate 28 end by a pair propeller (not shown) is closed in wherein said side, and described propeller comprises the hydraulic cylinder unit (not shown) being connected to side board support frame.The upper surface (so-called meniscus (" meniscus " level)) in casting molten bath 30 is usually located at the top of the lower end transmitting nozzle 26 thus the lower end transmitting nozzle is immersed in casting molten bath 30.The inside of casting roll 22 is with water-cooled thus make when casting roll is set on the roll surface of movement through casting molten bath shell, and the roll gap 27 introduced together between casting roll is sentenced and generated cast steel strip 12, and its roll gap between casting roll transmits downwards.
The type of double-roller continuous casting machine can be at United States Patent(USP) Nos. 5,184,668 and 5,277,243 or United States Patent (USP) 5,488,988 or U.S. Patent application 12/050, and the type describing in detail and record in 987.With reference to the patent specification of these patents and patent application, the suitable structure detail being applicable to the double-roller continuous casting machine of an embodiment of the present invention can be described, the disclosure in these patent specifications is quoted in this as cross reference.
Carry out rapid solidification by some parameters controlled in double-roller continuous casting machine, steel composition of the present invention creates MnO and SiO
2liquid deoxidation products, it is tiny and equally distributed globular inclusion.Due to limited hot drafts, existing MnO.SiO
2field trash is not also significantly elongated by continuous print course of hot rolling.Adjustable clamp foreign material/particle swarm is to stimulate the nucleation of acicular ferrite.MnO.SiO
2field trash can be about 10 μm of extremely very tiny particles (being less than 0.1 μm), and major part is about 0.5 μm ~ 5 μm.The non-metal field trash of the large-size of 0.5 ~ 10 μm is provided for nucleation acicular ferrite, and can comprise the mixture of field trash, such as, comprise MnS and CuS.Austenitic grain size is significantly greater than the austenitic grain size produced in conventional hot rolled strip.Thick austenitic grain size and combine the field trash/particle swarm regulated and contribute to the nucleation of acicular ferrite and bainite.
Continuous print hot-rolling mill 16 typically for 10 ~ 50% drafts.On runout table 17, cooling can comprise the gentle fog cooling in water cooling district (airmistcooling) thus control austenite transforms cooldown rate with temperature for when 300 ~ 700 DEG C realize needed for microscopic structure and material property.Alternatively, coiling temperature can be about 450 ~ 550 DEG C.The microstructure major part of gained comprises acicular ferrite and bainite.
In high-copper of the present invention and potassium steel, the impact of hot drafts on yield strength, tensile strength and general extension causes following Steel Properties: tensile strength during hot drafts in various degree, yield strength and general extension are more stable.In product made from steel so in the past, when hot drafts increases, yield strength and tensile strength will reduce usually.In contrast, in product made from steel of the present invention, the impact of hot drafts on yield strength, tensile strength and general extension significantly reduces.The hot rolling of high level can be combined to weaken the impact of hot drafts on mechanical performance lower than the coiling temperatures of 550 DEG C.
Hot drafts is greater than about 15% can bring out austenitic recrystallization, and it will reduce granularity and the volume fraction of acicular ferrite and bainite.
We have found that the recrystallization adding thick as cast condition (as-cast) austenitic grain size during the alloying element of quenching degree strengthening steel inhibits course of hot rolling, and after making hot rolling, keep the quenching degree of steel, thus thinner material can be produced, it has required microscopic structure and mechanical performance when hot drafts percentage in a big way.Below the content based on the steel composition in table 1 is discussed further,
table 1
| Steel | C | Mn | Si | Nb | V | N(ppm) |
| Basis (Base) | 0.02-0.05 | 0.7-0.9 | 0.15-0.30 | ＜0.003 | ＜0.003 | 35-90 |
| J | 0.19 | 0.94 | 0.21 | ＜0.003 | ＜0.003 | 85 |
| L | 0.033 | 1.28 | 0.21 | ＜0.003 | ＜0.003 | ＜100 |
The free oxygen content of the melting composition of steel J and L in table 1 be the composition of 41 ~ 54ppm and steel J and L comprise be greater than 0.01% and be less than or equal to 0.15% phosphorus.
The general composition of common carbon/manganese steel, the Fe content in such as, basis composition in table 1 is about 0.60 % by weight ~ 0.90 % by weight.We have developed steel composition (the steel L in table 1) that Fe content rolls up to strengthen the quenching degree of steel.Harden due to microstructural, the Fe content of increase provides required strength level.Extraly, the manganese in solid solution plays and suppresses deformation (deformed) austenitic Static Recrystallization (staticrecrystallization) after hot rolling, weakens the impact of hot drafts on mechanical performance.This inhibitory action may be realized by relatively conventional scale in short-term of producing based on (slab-based) of slab and the hot drafts of Min..Potassium steel of the present invention composition range degree under hot rolling be hot drafts up at least 35% time be more stable.This makes it possible to produce thinner and has the specification of required mechanical performance, and such as thickness is the steel L of 0.9mm.As shown in Figure 3, common 0.8% carbon/manganese grade of comparing, the less impact by measuring under hot rolling of yield strength of 1.28% manganese steel.In addition, the yield strength of 1.28% manganese is significantly higher than the yield strength of basic 0.8% manganese steel, and when hot rolling drafts is for being greater than 35%, its yield strength is more than 440Mpa.
After hot rolling, steel band is cooled to the coiling temperature of about 300 DEG C ~ 700 DEG C to provide the most microstructure comprising bainite and acicular ferrite.Alternatively, steel band is cooled to the coiling temperature of about 450 DEG C ~ 550 DEG C to provide the most microstructure comprising bainite and acicular ferrite.When the drafts of 15% and 35%, the difference in change of the mechanical performance of hot rolled strip in yield strength, tensile strength and general extension is within 10%.Alternatively, in the drafts scope of 15% ~ 35% difference in change of the mechanical performance of hot rolled strip in yield strength, tensile strength and general extension within 10%.
This composition can comprise be less than 0.25 % by weight carbon, the manganese of 0.9 % by weight ~ 2.0 % by weight, the silicon of 0.05 ~ 0.50 % by weight and be less than 0.01 % by weight aluminium.Alternatively, Fe content can be about 1.0 ~ 1.3 % by weight.
Alternatively or extraly, the composition of potassium steel can comprise at least one and be selected from following element: the niobium of about 0.01 % by weight ~ 0.2 % by weight, the molybdenum of about 0.05 % by weight ~ about 0.50 % by weight, about 0.01 % by weight ~ about 0.20 % by weight vanadium and their mixture.Also hot-dip can be carried out to provide the coating of zinc or kirsite or aluminium to hot rolled strip.
We have also found copper by adding 0.20 ~ 0.60 % by weight, keep manganese concentration to be above-mentioned minimum or be reduced to being low to moderate 0.08 % by weight and the tin that is less than 0.03 % by weight and the nickel that is less than 0.20 % by weight and can carrying out required microstructural hardening and reduce the impact of hot rolling drafts on mechanical performance.This high copper steel make it possible to by steel scrap (such as the steel scrap in bar milk) higher for copper content for steel-making in and without red brittleness.Cast the test melting material (trialheats) that a large amount of copper concentration ranges comprised is 0.2% ~ 0.4%, and cast and comprise one of about 0.6% bronze medal test melting material and do not produce red brittleness and it also avoid simultaneously and carry out specially treated (specialpractices) or add alloy.
The composition of cupric can comprise be less than 0.25 % by weight carbon, 0.2 ~ 2.0 % by weight manganese, 0.05 ~ 0.50 % by weight silicon, be less than 0.01 % by weight aluminium, be less than 0.03 % by weight tin, be less than the nickel of 0.10 % by weight and the copper of 0.20 ~ 0.60 % by weight.Alternatively, copper content can be about 0.2 % by weight ~ 0.5 % by weight, and alternatively, can be about 0.3 % by weight ~ 0.4 % by weight.Again, the free oxygen content of casting molten steel (moltensteelcast) is 20 ~ 75ppm and free oxygen content can be 30 ~ 60ppm.Again, total oxygen concentration is 70ppm ~ 150ppm.
Hot rolled strip additionally can comprise the chromium content of about 0.4 % by weight ~ 0.75 % by weight.Alternatively, chromium content can be about 0.4 % by weight ~ 0.5 % by weight.
The tin utilizing the quenching degree of suitable increase that provided by copper and be less than 0.03% and the nickel that is less than 0.20% strength grade (grade SS380) that generation is higher when the low coiling temperature of high cooldown rate and about 500 DEG C ~ 600 DEG C.Alternatively, lower strength grade can produce the impact of offsetting copper content and increasing with high-copper when low cooldown rate and high coiling temperature.As shown in table 2, copper content is the zinc-plated structural class (galvanizedstructuralgrades) that the tensile property of the grade of 0.20% ~ 0.40% produces certain limit, and such as grade SS275 is to grade SS380.
table 2
In order to produce the comparatively low-intensity grade of high-copper, use the higher coiling temperature of about 600 ~ 700 DEG C to offset the copper content increased.By batching when the temperature of increase, high copper steel of the present invention can provide the physical property being similar to the common carbon/manganese steel with low copper content.The steel composition with copper concentration of the present invention with the manufacture of high-copper steel scrap in electric arc furnaces, as mentioned above, compared with the low copper steel scrap of use, can significantly reduce cost like this.
Alternatively, height copper steel spelter coating of the present invention or Zinc alloy coated in one or both or aluminized coating carry out hot-dip, such as galvanizing coating,
with
coating, coating of aluminizing or other coatings.When temperature of steel strips remains the A far below steel
c1during temperature, the microstructure of hot-dip height copper steel of the present invention does not have significant change.Therefore, the mechanical performance of the uncoated high copper steel under hot-rolled condition is similar to the mechanical performance to carry out coating in Continuous Hot Dip Galvanizing Line after.
Alternatively or extraly, the composition of high-copper can comprise at least one and be selected from following element: the niobium of about 0.01 % by weight ~ 0.2 % by weight, the molybdenum of about 0.05 % by weight ~ about 0.50 % by weight, about 0.01 % by weight ~ about 0.20 % by weight vanadium and their mixture.
In arbitrary situation, the concentration of carbon of about 0.20% and the concentration of carbon of Geng Gao also may be used for not needing in the application of microalloying.In addition, the higher concentration of carbon of 0.30 ~ 0.50% may be used for some material thicknesses is in the application of 1.0 ~ 1.5mm.In the past, these high-carbon steel needs repeatedly to anneal with cold rolling step to realize such thickness.
0.19% carbon steel composition is given in table 1 (steel J) and mechanical performance is shown in Figure 4 as the function of used hot rolling drafts.The strength level of the present invention 0.19% carbon steel is higher than existing ordinary low-carbon steel.As shown in Figure 4, when the coiling temperature in routine adds man-hour, yield strength under used whole hot rolling in weight range for being greater than 380Mpa.This and mild steel (0.02-0.05%C) form contrast, use lower coiling temperature and limited hot rolling drafts to provide the yield strength being greater than 380Mpa in mild steel.
The extra sample of steel of the present invention uses the manganese of about 0.88% ~ 1.1% and the carbon amounts of about 0.02% ~ 0.04% to be prepared, as shown in Figures 5 and 6.As shown in Figure 5, tensile strength, yield strength and general extension are more stable when manganese amount is the variable concentrations of 0.88% ~ 1.1%.
In steel of the present invention, the impact of hot drafts on yield strength, tensile strength and general extension result in following Steel Properties: tensile strength during the hot drafts of varying level, yield strength and general extension are more stable, as shown in Figure 6.As mentioned above, in former this kind of product made from steel, when hot drafts increases, yield strength and tensile strength can reduce usually.In contrast, in product made from steel of the present invention, the impact on yield strength, tensile strength and general extension of the hot drafts of different amount significantly reduces.As shown in Figure 6, steel of the present invention is more stable when under the hot rolling of drafts up at least 45%, range is spent.Hot rolled strip 300 ~ 700 DEG C, alternatively for the temperature cooling of about 450 ~ 550 DEG C after the most microstructure containing bainite and acicular ferrite is provided, and there is difference in change that performance makes mechanical performance when drafts is 10% and 35% in yield strength, tensile strength and general extension within 10%.Alternatively, mechanical performance during drafts in 10% ~ 35% scope for yield strength, tensile strength and general extension within 10%.Again in addition optionally, drafts be 15 and 35% time the difference in change of mechanical performance in yield strength, tensile strength and general extension be within 10%.Alternatively, the difference in change of mechanical performance during drafts in 15 ~ 35% scopes in yield strength, tensile strength and general extension is within 10%.
Explain in above-mentioned drawing and description and describe the present invention; it is exemplary and nonrestrictive in characteristic aspect; should be understood that the exemplary embodiment only illustrating and describe them, and need all changes in the spirit of the present invention of protection described in following claim and amendment.On the basis considering this description, additional features of the present invention is apparent for one skilled in the art.Can to modify and without departing from the spirit and scope of the present invention.
Claims (18)
1. a hot rolled strip, it is by comprising the following steps to manufacture:
Assembling inner cooling type roller conticaster, it has the casting roll being positioned at side, roll gap is formed between casting roll, and form the casting molten bath of molten steel, described casting molten bath to be supported in the casting roll above roll gap and to be limited near casting roll end by side shield, described molten steel has the free oxygen content of 20 ~ 75ppm, its composition makes the composition of described hot rolled strip comprise the carbon being less than 0.25 % by weight, be greater than 0.01 % by weight and be less than or equal to 0.15 % by weight phosphorus, be less than the tin of 0.03 % by weight, be less than the nickel of 0.20 % by weight, the manganese of 0.2 ~ 2.0 % by weight, the silicon of 0.05 ~ 0.50 % by weight, be less than the aluminium of 0.01 % by weight and the copper of 0.20 ~ 0.60 % by weight,
Reversely rotate described casting roll and to make when described casting roll moves through described casting molten bath solidify metal shells in casting roll,
Described roll gap between casting roll is moved downward through to form steel band by described metal-back,
Steel band described in hot rolling in the scope of 10 ~ 50%, the quenching degree that the copper of 0.2 ~ 0.6% in described steel provides thus makes the mechanical performance through hot rolled strip when drafts is 10% and the mechanical performance through hot rolled strip when drafts is 35% difference in change in yield strength, tensile strength and general extension within 10%; And
Hot rolled strip is batched to provide the most microstructure containing bainite and acicular ferrite the temperature of 300 ~ 700 DEG C.
2. hot rolled strip according to claim 1, its step by described hot rolled strip and manufacturing, the mechanical performance through hot rolled strip thus when drafts is 15% and the difference in change of the mechanical performance through hot rolled strip when drafts is 35% in yield strength, tensile strength and general extension are within 10%.
3., according to hot rolled strip according to claim 1 or claim 2, the free oxygen content of wherein said molten steel is 30 ~ 60ppm.
4. hot rolled strip according to claim 1, wherein said copper content is 0.2 ~ 0.5 % by weight.
5. hot rolled strip according to claim 1, wherein said copper content is 0.3 ~ 0.4 % by weight.
6. hot rolled strip according to claim 1, wherein said nickel content is for being less than 0.1 % by weight.
7. hot rolled strip according to claim 1, batches at the temperature of 600 ~ 700 DEG C.
8. hot rolled strip according to claim 1, the chromium content that it comprises is 0.4 ~ 0.75 % by weight.
9. hot rolled strip according to claim 1, the chromium content that it comprises is 0.4 ~ 0.5 % by weight.
10. manufacture a method for hot rolled strip, its step comprises:
Assembling inner cooling type roller conticaster, it has the casting roll being positioned at side, roll gap is formed between casting roll, and form the casting molten bath of molten steel, described casting molten bath to be supported in the casting roll above roll gap and to be limited near casting roll end by side shield, described molten steel has the free oxygen content of 20 ~ 75ppm, its composition makes the composition of described hot rolled strip comprise the carbon being less than 0.25 % by weight, be greater than 0.01 % by weight and be less than or equal to 0.15 % by weight phosphorus, be less than the tin of 0.03 % by weight, be less than the nickel of 0.20 % by weight, the manganese of 0.2 ~ 2.0 % by weight, the silicon of 0.05 ~ 0.50 % by weight, be less than the aluminium of 0.01 % by weight and the copper of 0.20 ~ 0.60 % by weight,
Reversely rotate described casting roll and to make when described casting roll moves through described casting molten bath solidify metal shells in casting roll,
Described roll gap between casting roll is moved downward through to form steel band by described metal-back,
Steel band described in hot rolling in the scope of 10 ~ 50%, the quenching degree that the copper of 0.20 ~ 0.60% in described steel provides thus makes the mechanical performance through hot rolled strip when drafts is 10% and the mechanical performance through hot rolled strip when drafts is 35% difference in change in yield strength, tensile strength and general extension within 10%; And
Hot rolled strip is batched to provide the most microstructure containing bainite and acicular ferrite the temperature of 300 ~ 700 DEG C.
The method of 11. manufacture hot rolled strips according to claim 10, it comprises the mechanical performance through hot rolled strip that steel band described in hot rolling makes steel band when drafts is 15% and the difference in change step 10% within of the mechanical performance through hot rolled strip in yield strength, tensile strength and general extension when drafts is 35%.
12. according to the method for claim 10 or manufacture hot rolled strip according to claim 11, and the free oxygen content of wherein said molten steel is 30 ~ 60ppm.
The method of 13. manufacture hot rolled strips according to claim 10, the composition of wherein said molten steel makes the copper content of described hot rolled strip be 0.2 ~ 0.5 % by weight.
The method of 14. manufacture hot rolled strips according to claim 10, the composition of wherein said molten steel makes the copper content of described hot rolled strip be 0.3 ~ 0.4 % by weight.
The method of 15. manufacture hot rolled strips according to claim 10, the composition of wherein said molten steel makes the nickel content of described hot rolled strip for being less than 0.1 % by weight.
The method of 16. manufacture hot rolled strips according to claim 10, wherein said coiling temperature is 600 ~ 700 DEG C.
The method of 17. manufacture hot rolled strips according to claim 10, the composition of wherein said molten steel makes the chromium content of described hot rolled strip be 0.4 ~ 0.75 % by weight.
The method of 18. manufacture hot rolled strips according to claim 10, the composition of wherein said molten steel makes the chromium content of described hot rolled strip be 0.4 ~ 0.5 % by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510522890.7A CN105215299A (en) | 2009-02-20 | 2010-02-20 | Hot rolled thin cast steel strip product and manufacture method thereof |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US15423309P | 2009-02-20 | 2009-02-20 | |
| US61/154,233 | 2009-02-20 | ||
| PCT/AU2010/000189 WO2010094076A1 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510522890.7A Division CN105215299A (en) | 2009-02-20 | 2010-02-20 | Hot rolled thin cast steel strip product and manufacture method thereof |
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| Publication Number | Publication Date |
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| CN102325608A CN102325608A (en) | 2012-01-18 |
| CN102325608B true CN102325608B (en) | 2015-11-25 |
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| Application Number | Title | Priority Date | Filing Date |
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| CN201080008606.XA Active CN102325608B (en) | 2009-02-20 | 2010-02-20 | Hot rolled thin cast steel strip product and manufacture method thereof |
| CN201510522890.7A Pending CN105215299A (en) | 2009-02-20 | 2010-02-20 | Hot rolled thin cast steel strip product and manufacture method thereof |
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| Application Number | Title | Priority Date | Filing Date |
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| CN201510522890.7A Pending CN105215299A (en) | 2009-02-20 | 2010-02-20 | Hot rolled thin cast steel strip product and manufacture method thereof |
Country Status (10)
| Country | Link |
|---|---|
| US (1) | US20100215981A1 (en) |
| EP (2) | EP3431201A3 (en) |
| JP (1) | JP5509222B2 (en) |
| KR (1) | KR101715086B1 (en) |
| CN (2) | CN102325608B (en) |
| AU (2) | AU2010215077B2 (en) |
| MY (1) | MY173389A (en) |
| PL (1) | PL2398602T3 (en) |
| RU (1) | RU2532794C2 (en) |
| WO (1) | WO2010094076A1 (en) |
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| DE102010010536B4 (en) * | 2010-03-05 | 2017-01-05 | Theodor Stuth | Process for the production of nickel strip |
| US20140261905A1 (en) * | 2013-03-15 | 2014-09-18 | Castrip, Llc | Method of thin strip casting |
| CN104959561B (en) * | 2015-07-09 | 2017-12-01 | 东北大学 | A kind of method for improving double roller continuous casting low-carbon micro steel-alloy acicular ferrite content |
| CN112522588B (en) * | 2019-09-19 | 2022-06-28 | 宝山钢铁股份有限公司 | Method for producing high-strength thin-specification patterned steel plate/strip through thin strip continuous casting |
| CN112522629B (en) * | 2019-09-19 | 2022-06-24 | 宝山钢铁股份有限公司 | Nb microalloying high-strength high-hole-expansion steel and production method thereof |
| WO2023062643A1 (en) * | 2021-10-13 | 2023-04-20 | Stephen Fernandes | Slip planes in metal and mechanical strength in materials |
| CN115478203A (en) * | 2022-09-27 | 2022-12-16 | 张家港中美超薄带科技有限公司 | Method for producing hot-rolled thin strip steel based on thin strip casting and rolling and ultrahigh-strength part |
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Also Published As
| Publication number | Publication date |
|---|---|
| KR101715086B1 (en) | 2017-03-10 |
| JP5509222B2 (en) | 2014-06-04 |
| RU2532794C2 (en) | 2014-11-10 |
| KR20110117142A (en) | 2011-10-26 |
| PL2398602T3 (en) | 2019-04-30 |
| AU2017202997B2 (en) | 2019-01-17 |
| AU2010215077B2 (en) | 2017-05-25 |
| AU2017202997A1 (en) | 2017-06-01 |
| CN105215299A (en) | 2016-01-06 |
| WO2010094076A1 (en) | 2010-08-26 |
| EP3431201A2 (en) | 2019-01-23 |
| AU2010215077A1 (en) | 2011-07-28 |
| EP2398602A1 (en) | 2011-12-28 |
| MY173389A (en) | 2020-01-22 |
| EP2398602A4 (en) | 2014-09-24 |
| CN102325608A (en) | 2012-01-18 |
| RU2011138463A (en) | 2013-03-27 |
| US20100215981A1 (en) | 2010-08-26 |
| EP3431201A3 (en) | 2019-03-13 |
| EP2398602B1 (en) | 2018-10-31 |
| JP2012518539A (en) | 2012-08-16 |
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