CN103328120B - The method manufacturing hot rolled steel plate product - Google Patents
The method manufacturing hot rolled steel plate product Download PDFInfo
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- CN103328120B CN103328120B CN201180064797.6A CN201180064797A CN103328120B CN 103328120 B CN103328120 B CN 103328120B CN 201180064797 A CN201180064797 A CN 201180064797A CN 103328120 B CN103328120 B CN 103328120B
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- steel
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- hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- 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
-
- 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
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/1213—Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Abstract
The present invention provides a kind of method being manufactured steel sheet product by steel in the way of economical and reliably controlled, and this steel is except high Mn content is possibly together with high Al content。The method according to the invention comprises the steps of and is melted by molten steel (S), molten steel is except Fe and inevitable impurity are possibly together with (weight %) C:0.5-1.3%, Mn:18-26%, Al:5.9-11.5%, Si:< 1%, Cr:< 8%, Ni:< 3%, Mo:< 2%, N:< 0.1%, B:< 0.1%, Cu:< 5%, Nb:< 1%, Ti:< 1%, V:< 1%, Ca:< 0.05%, Zr:< 0.1%, P:< 0.04%, S:< 0.04%；Molten steel casting is become the steel band being cast；With the rate of heat addition of at least 20K/s, the steel band being cast is heated to the hot rolling initial temperature of 1100-1300 DEG C；Would be heated to the Band by Hot-rolling being cast of hot rolling initial temperature and become hot rolled strip；Start the cooldown rate with at least 100K/s in 10s after hot rolling and hot rolled strip is cooled to < 400 DEG C；At the spooling temperature less than 400 DEG C, cooled hot rolled strip spooling is become coiled material。
Description
Technical field
The present invention relates to a kind of method manufacturing hot rolled steel plate product, this hot rolled steel plate product is made up of the manganese steel of high intensity, high ductibility, and this manganese steel also comprises the Al content of 5.9-11.5 weight % except high Mn content。
Background technology
This steel and its manufacture method are such as known in DE-AS1262613。Become there is the steel ingot of minor diameter by the molten steel casting with corresponding constituent according to the method described in that publication, subsequently steel ingot is rolled into bar stock。Ductility and the notch impact strength of the steel so prepared can be improved by the heat treatment of 800-1250 DEG C。The bar stock so prepared can be used in manufacturing the part of aircraft, guided missile, turbine, change speed gear box, valve and similar machinery。
More recently development shows, starts the steel of described type due to high intensity, good morphotropism, significantly reduced density and the extraordinary combining properties of the weight minimized thus caused and is highly suitable as plate product (i.e. steel plate or steel band) for manufacturing the part of motor vehicles particularly body of a motor car or automobile chassis。
But problem is, described steel is difficult to be processed by traditional production technology (being such as typically used in the production technology in the steel of high-carbon content) owing to its alloy forms situation。Therefore known steel has core isolation (Kernsegregation) trend of Mn and the Al of raising in casting and condensation process。This external this kind of known steel also exists higher risk, bends backward when namely producing face crack and steel Shu Cong mold are derived in continuous casting。Additionally due to the weak capacity of heat transmission of this known steel typically requires long preheating, so that being reached the temperature required for hot rolling by the above-mentioned fluid origin slab of steel。Along with significant skin decarburization trend occurs in slab stopping for a long time in stove。The simultaneously weak capacity of heat transmission itself brings problem, namely is likely to generate gap due to the recrystallization inertia of the relatively low strip edge of temperature in preheating, breaking down and course of hot rolling。Last this steel hot rolling and cold rolling in present very high hot rolling resistance or cold rolling resistance, hence it is evident that higher than other high-alloy steel (such as RSH steel or traditional high alloy Mn steel)。
Known a kind of by this traditional components by US7794552B2, austenitic, the method that the hot-rolled steel of high violent content manufactures steel sheet product, this hot-rolled steel is also possible to the C containing (weight %) 0.85-1.05% except ferrum and inevitable impurity, the Mn of 16-19%, the Si of the highest 2%, the Al of the highest 0.050%, the S of the highest 0.030%, the P of the highest 0.050%, the N and optional group of " Cr of the highest 0.1%, Mo, Ni, Cu, Ti, Nb, V " in one or more there is the element of following content: Cr content is the highest by 1%, Mo content is the highest by 1.5%, Ni content is the highest by 1%, Cu content is the highest by 5%, Ti content is the highest by 0.50%, Nb content the highest 0.50% and V content are the highest by 0.50%。Obtained steel plate or the surface share of the recrystallization of steel band should be equal to 100%, and the surface share of the carbide precipitated out should be 0%。Simultaneously the average grain size of steel should≤10 μm。The intensity of the known steel so made should should more than 65000MPa more than the product of 1200MPa and intensity and maximal tensility。
In order to realize above-mentioned character, according to known method, the molten steel with corresponding component being cast as semi-finished product, these semi-finished product can be slab, sheet billet or cast strip。Semi-finished product are heated to the temperature of 1100-1300 DEG C and are rolled into hot rolled strip under the hot-rolled temperature of at least 900 DEG C。Then the retention time of one section of desired recrystallization completely enough reaching steel strip surface is kept if desired。Then the hot rolled strip so obtained is cooled to the spooling temperature of the highest 400 DEG C with the cooldown rate of at least 20 DEG C/s and spooling becomes coiled material。The hot rolled strip so made is rolled into cold-rolled strip by the annealing and then can inserted in one or more cold rolling step and if desired。
Being applicable to this steel by method known for US7794552B2, although can add Al to subtract oxygen in the melting thing of this steel, but the content of Al is limited to the highest 0.05 weight %, to avoid the precipitation of AlN。The appearance of AlN precipitate can bring the danger of the generation in the crack in the deformation process of the steel band made at known method。
Summary of the invention
Under the background of foregoing prior art, it is an object of the invention to, provide one and manufactured method steel sheet product, economical and reliably controlled by steel (it is except high Mn content is possibly together with high Al content)。
Realized by the method provided in claim 1 according to this purpose of the present invention。The favourable form of implementation of the method according to the invention provides in the dependent claims。
According to the present invention, first being melted by steel to manufacture the steel sheet product of hot rolling, this steel is except ferrum and inevitable impurity are possibly together with (weight %) C:0.5-1.3%, Mn:18-26%, Al:5.9-11.5%, Si:0.1-0.4%, Cr: less than 8%, Ni: less than 3%, Mo: less than 2%, N: less than 0.1%, B: less than 0.1%, Cu: less than 5%, Nb: less than 1%, Ti: less than 1%, V: less than 1%, Ca: less than 0.05%, Zr: less than 0.1%, P: less than 0.04%, S: less than 0.04%。
Silicon addition in the practical design of the present invention, Cr, Ni, Mo, N, B, Cu, Nb, Ti, V, Ca, Zr, the content of P and S can individually or in combination with each other be adjusted to following amount (weight %): the Cr of < 3.0%, the Ni of < 1.0%, the Mo of < 0.5%, the N of 0.005-0.04%, the B of < 0.0050%, the Cu of < 1%, the Nb of < 0.2%, the Ti of < 0.3%, the V of < 0.3%, the Ca of < 0.005%, the Zr of < 0.005%, the S of P or 0.005-0.02% of 0.01-0.03%。
Then the molten steel formed in the way of given above is such as cast as cast steel strip in a way known in two traditional steps rolling casting machines。
Known molten steel casting become the advantage of cast steel strip be in that, owing to quickly solidification is so there is less isolation in the casting process of steel band。This is particularly advantageous in the high-alloy steel of the type carrying out processing according to the present invention, because being capable of uniform steel band character and the optimum quality of the product obtained by the average distribution of alloying element。
If needing to use two traditional step rolling casting machines to manufacture cast steel strip, the steel band being wherein cast is with vertical direction output and changes, by steel bundle guide, the conveying direction that route is level in arc section, and the steel band being so cast generally is cooled to be not less than in principle the medium temperature of 700 DEG C with the cooldown rate of 10-20K/s on its road from casting machine to heater。Controlling as far as possible little according to the present invention by this temperature leak, the steel being so cast is carried in heater as much as possible at casting heat out intrinsic afterwards from casting machine。Can make by this way in heater, be down to minimum for the energy needed for temperature here is brought up to hot rolling initial temperature。
The process of the hot rolling initial temperature being heated within the scope of 1100-1300 DEG C by the steel band through casting carries out with the rate of heat addition of at least 20K/s according to the present invention。
Next the steel band being cast so being heated rapidly to hot rolling initial temperature is rolled into hot rolled strip in one or several passages。
Come into effect cooling according in present invention 10s after hot rolling terminates, wherein obtained hot rolled strip is cooled to < 400 DEG C with the cooldown rate of at least 100K/s。The generation of the component (such as carbide or intermetallic phase) with embrittling effect is inhibited by quickly cooling。
Finally the hot rolled strip of cooling spooling at the spooling temperature of the highest 400 DEG C is become coiled material。
Each procedure of processing of the method according to the invention carries out in the operation that a continuous print does not interrupt。
The present invention is from this understanding, namely, if being cast as steel band thin, the thickest 5mm, the particularly thickness of 3-5mm by the molten steel of respective components, then be capable of being made up of the steel containing the C of high-load, Mn and Al that edge is seamless and the steel sheet product of seamless surface。In the scope of the thickness that the thickness of the steel band being so cast just should have at the hot rolled steel plate product completing to manufacture。
The method applied in the method according to the invention, namely casts out in casting steel strip technique (Bandguss) and has the frequency of the core isolation that the C of high-load, the steel of Al and Mn and the rapid solidification of consequential steel after the casting decrease in the steel band being cast。Entirely without transverse crack and star shake occur in the casting process of the steel band being cast, and the appearance quantity of longitudinal crack is also greatly reduced。Can pass through to cast the appearance of the change regulation and control core isolation of rolling force when two steps roll cast steel strip in casting machine。Thin, when it leaves casting gap, just there is favourable cross section (having less bending stress) according to the thickest steel plate being cast for 5mm (preferred 3-5mm) of the present invention。Correspondingly, the steel band through casting can successfully be turned from vertical conveying direction the conveying direction of level, and the steel being cast on the conveying direction of level is by other stations in its procedure of processing。
Simultaneously by using belt welding to significantly reduce surface decarburization phenomenon, because being no longer necessary to long heating of plate blank。Due to homogenization Temperature Distribution (according to the present invention quickly carried out before hot rolling add hanker realizing) to make the danger of cracking initiation in the hot rolling be down to minimum。
Steel band according to present invention casting is characterized by the cast structure of the three layers of dendritic border and spherical core。
The steel band being cast applies its hot rolling initial temperature being heated to required 1100-1300 DEG C when casting heat energy of self when leaving casting machine when as much as possible。Wherein it is done as quickly as possible heating, particularly with the rate of heat addition of at least 20K/s。
Adding that to hanker the scope that the typical temperature that reaches in the steel band being cast improves be until 250 DEG C according to of the invention process, wherein typical minimum temperature rises to 50 DEG C。Heated by the steel band of the Rapid Implementation according to the present invention, except it can be avoided that the generation of undesirable precipitation can also on purpose adjust the Temperature Distribution on the width of whole steel band。Therefore achieve on the one hand and make uniformity of temperature profile by quickly heating。In order to realize some deformational behavior determined of the steel band being cast in the hot rolling, heating can be implemented on the other hand, the whole width of the steel band being cast adjusts a temperature profile distribution determined。Other geometric error of the deviation on the out-of-flatness of steel band, straight line stability and steel band can be minimized by this way, without applying extra measure or needing extra instrument。
Particularly the firing equipment (equipment as described in DE10323796B3) of induction mode work is heated to hot rolling initial temperature with being suited to speed up。Quickly heating or completely heated up advantage that electric induction furnace is applied to article to be rolled are in that, it is possible to being heated to by rolled goods within short action time can relatively precisely predetermined temperature。
So select the hot rolling initial temperature reached in rapid heating process, make the rolling resistance hindering the steel band being cast in the hot rolling be minimized。Particularly when hot rolling initial temperature is minimum be 1050 DEG C time。Hot rolling final temperature according to hot rolling of the invention process is typically located in the scope of 1000-1050 DEG C。These parameters based on, must be processed in very narrow temperature range due to its high aluminum content according to the steel that the present invention is processed。
The hot rolling of the steel band being cast carried out in casting steel strip processing line decreases the particular procedure of cast steel strip and certain material core porous, promotes that the uniformity of micro structure is thus generally improving steel band performance。
The hot rolling of the steel band being cast of very difficult rolling itself can thus simplify extraly, and the steel band being cast before hot rolling has just had the thickness close to final size, thus only must carry out relatively low degree of deformation in the hot rolling。Degree of deformation is typically minimum 10%, particularly 10-20%。So low degree of deformation can realize in a passage, and this optimizes the economy of the method according to the invention by additionally facilitating。
Ensure that the growth of crystal grain does not occur after leaving last hot-rolling mill frame in obtained hot rolled strip by the quickly cooling (cooldown rate is 100K/s at least) implemented after hot rolling。In addition the precipitation of carbide, nitride and carbonitride is also avoided by this way in this position of the method according to the invention。The cooldown rate that the cooling implemented after hot rolling reaches typically lies in the scope of 100 to 250K/s。
In order to reliably avoid the generation of grain growth, hot rolling should proceed by cooling after terminating after interval short as far as possible, the longest for 10s。
In order to avoid the oxidation on the road going to hot-rolling arrangement of the oxidation of molten steel and the steel band that is cast, it is possible to carry out the procedure of processing carried out before hot rolling in the method according to the invention in protective gas atmosphere。The deactivation that the bent moon region of the molten steel treating casting implemented in each belt casting apparatus carries out decreases the generation of the oxide layer on surface。
Having austenite ferrite fabric according to the hot rolled strip that the present invention obtains, ferrite share is typically 5-50%。
Can exist with the content of 0.5 to 1.2 weight % according to the carbon in the steel of the present invention, wherein be related specifically to the C content steel higher than 0.5 weight % here。Due to the generation of solution strengthening, the raising of stacking fault energy and carbide, C content is extremely important for forming austenite and strength grade。Once hot rolled strip constructed in accordance is cold rolled to cold-rolled strip, the yield limit in order to improve cold-rolled strip can precipitate out very fine carbide by purpose carrying out overaging process after full annealed step last on cold-rolled strip。If C content is more than 1.2 weight %, there is the danger producing to cause the carbide of the amount of embrittlement。
The content of the manganese existed in the steel according to present invention processing is 18-26 weight %。Manganese is critically important for austenitic generation and improves stacking fault energy (machinability and deformability are played advantageous effect by it)。
Steel according to present invention processing has the Al of 5.9-11.5 weight %, particularly > 6-11.5 weight %。Aluminum reduces density, causes solution strengthening and improves stacking fault energy。In addition aluminum has passivation effect and improves corrosion resistance。The Al of high-load due to very high stacking fault energy cause so-called " shear band plasticity (shearbandplasticity) " (as have extraordinary, intensity and deformability combination, the deformation mechanism with advantage) obvious generation。But too high aluminum content can cause the DO of the serious embrittlement in ferrite3Structure or the excessive k-carbide ((Fe, Mn) containing Al causing embrittlement3AlC)。
The content of the Si existed in the steel according to present invention processing is less than 1 weight %, particularly 0.1-0.4 weight %, to cause solution strengthening。But content more than the Si of 1 weight % make according to the present invention processing steel weldability and can coating be deteriorated。
Cr, Ni and Mo cause solution strengthening equally and improve the non-oxidizability of steel according to present invention processing and corrosion resistance。But the Cr of too high amount causes causing the generation of strong brittle alloy carbide。When such as the present invention provides, limit according in the steel of present invention processing: Cr content, less than 8 weight %, is especially less than 3 weight %；Ni content, less than 3 weight %, is especially less than 1 weight % and Mo content less than 2 weight %, when being especially less than 0.5 weight %, Cr, Ni and Mo advantageous effect can obtain the best utilization。
Nitrogen forms nitride with aluminum and causes intensity to increase。But the N of too high amount causes oarse-grained AlN, it is likely to be unfavorable for according to the machinability of steel of present invention processing, superficial makings and deformability。Therefore it is limited to N < 0.1 weight %, particularly 0.005-0.04 weight % according to the N content of the steel of the present invention。
The B content of the steel according to the present invention is limited to < 0.1 weight %, is especially less than 0.0050 weight %。B causes intensity to increase and forms boron nitride or the boron carbide of nucleating point as the carbide for generating other。Too high B content causes embrittlement due to grain boundary precipitate。
Cu causes solution strengthening in the steel processed according to the present invention and improves corrosion resistance。But too high Cu content is joined to the danger that there is " thermal crack(ing " in process in thermal deformation or hot charging。Therefore the Cu content according to the steel of present invention processing is limited to less than 5 weight %, is especially less than 1 weight %。
Microalloy element Nb, Ti and V cause that isolation and crystal grain miniaturization hence help to the increase of intensity。In addition these elements join the trend of the weld crack passing through the fine declines steel of crystal grain in process at hot charging。It is respectively smaller than Nb, Ti or V of 1.0 weight % when the steel processed according to the present invention has content, particularly limit: Nb content < 0.2 weight %, Ti content < 0.3 weight %, when V content < 0.3 weight %, this effect can obtain the utilization of the best。
Content makes nonmetallic materials such as Al less than the Ca of 0.05 weight %, particularly < 0.005 weight % in the steel processed according to the present invention2O3With FeS nodularization (speroidiziert), and improve deformability。Alumina conversion is become slag and improves purity by the formation of calcium aluminate。
Content causes the solution strengthening of the steel processed according to the present invention less than 0.1 weight %, the particularly Zr of < 0.005 weight %。But it is because Zr, due to crystal boundary isolation, there is embrittling effect, so the steel according to present invention processing has restriction for the content of this element。
In the steel processed according to the present invention, P and S separates crystal boundary and causes embrittlement。Therefore the content of the two should lack as much as possible, is especially less than 0.04 weight %, and wherein P content is advantageously located at 0.01-0.03 weight % and S content is advantageously located at 0.005-0.02 weight %。
In order to ensure the best deformability of the hot rolled strip obtained according to the present invention, it is possible to carrying out hot band anneal before being processed further after spooling, the hot rolled strip wherein obtained according to the present invention is annealed under the annealing temperature of 1100-1200 DEG C。If carrying out the annealing of hot rolled strip in continuous annealing furnace, then need the annealing time of 60-300s。If according to the Al content of the steel of present invention processing is at least 10 weight %, such hot band anneal is particularly advantageous。Such high Al content also helps the generation avoiding brittlement phase, cools down as soon as possible after hot rolling, particularly with the cooling rate of at least 40K/s。
Alternatively the hot rolled strip obtained according to the present invention can be carried out in a conventional manner pickling and carry out when non-coating or coating after spooling。Equally possible after the optional pickling carried out in a way known with metal, such as erosion-resisting protective layer hot rolled strip constructed in accordance is carried out coating。In addition it is contemplated that hot rolled steel plate product constructed in accordance is arranged coating, the deformation of hot rolled strip is simplified by this coating。
The hot rolled strip obtained according to the present invention can being cold rolled to cold-rolled strip product by steps of a method in accordance with the invention, finally this cold-rolled strip product can through the various deformation operation (Z, ZE, ZN, FAL) of full annealed, overaging annealing (by fine silicon carbide thing precipitation-hardening) and Surface Finishing。Cold rolling and final full annealed presses solidly and makes the micro structure homogenization in core region。
If needing steel sheet product to have less thickness, then in one or more passage, the hot rolled strip obtained according to the present invention to be processed into cold-rolled strip in a way known。Cold-rolled strip can carry out face coat when necessary again, thus protecting it from protected from environmental。
Due to already close to final size the steel band that casts and thus cause have only to only small deformation, high hot rolling resistance intrinsic in the steel processed according to the present invention and cold rolling resistance hot rolling and cold rolling in only serve inappreciable effect。This allow that, by view of rolling processing, the steel sheet product with little thickness made by problematic steel according to the type of present invention processing itself。
Accompanying drawing explanation
Next it is further elucidated with the present invention according to embodiment。
Fig. 1 generally show the production line 1 for manufacturing hot rolled strip W。
Description of reference numerals
1 production line
2,3 casting roll
4 conveyer devices
5 heaters
6 induction apparatuss
9 rolling-mill housing
10 chillers
11 coilers
A protective gas atmosphere
C coiled material
F conveying direction
The steel band that G is cast
S molten steel
U environment
W hot rolled strip
Detailed description of the invention
The production line 1 designed for the production procedure of realization in continuous print process flow comprises two traditional steps rolling casting devices 1, being cast as, in the casting gap that wherein molten steel S limits between two casting rolls rotated in opposite directions 2,3, the steel band G being cast, the thickness of steel band is typically 3-5mm。The steel band G being cast flowed out in the vertical direction redirect to the conveying direction F of level with same per se known manner by steel bundle guide, is advanced by steel band by the conveyer device 4 being placed in steel bundle guide end on the conveying direction of level。
The steel band G being cast so being arranged on conveying direction F movement enters in heater 5。The steel band G being cast is cooled to medium temperature with cooldown rate 10-20K/s on the road that it goes to heater 5。
The steel band G being cast entered herein with medium temperature is heated to hot rolling initial temperature by the induction apparatus 6 lying across conveying direction F orientation by heater 5 in the way of sensing, hot rolling initial temperature is typically located within the scope of 1100-1300 DEG C, particularly at least 1150 DEG C。
In process flow by heater by the electromagnetic field manufactured by induction apparatus 6 effect realize the steel band G being cast temperature promote be up to 300 DEG C, be typically 50-150 DEG C。Wherein can so adjust and control sensor 6 (as described in DE10323796B3), the steel band G being cast on the one hand can be heated equably on its whole width, can on purpose adjust a temperature profile curve on the other hand in the steel band G being cast。
In order to avoid contacting of molten steel S and steel band G and the environment U being cast, two steps are rolled casting devices 1, steel bundle guide, conveyer device 4 and heater 5 and is maintained in protective gas atmosphere S。
And then the steel band G that heater 5 place is cast enters rolling-mill housing 9, is here rolled in a passage by steel band and has the hot rolled strip W that typical thickness is 2.4-4.5mm。Hot rolled strip W leaves the hot rolling final temperature being positioned at last rolling-mill housing 9 on conveying direction F generally 1000-1050 DEG C of scope。The degree of deformation realized by a rolling pass is usually located within the scope of 10-30%。
From rolling-mill housing 9 out after 10s in chiller 10 cooldown rate to be typically 100-200K/s start, by the obtained hot rolled strip W spooling temperature being cooled within the scope of 300-400 DEG C, then in coiler 11, with this spooling temperature spooling, hot rolled strip W to be become coiled material C。
Unshowned annealing device can carry out herein the annealing of hot rolled strip after spooling processes。
In production line 1, manner described above is made for four hot rolled strips by molten steel S1-S3, and the constituent of molten steel provides in table 1。
Cooled down with the cooldown rate of about 15K/s respectively on the road going to heater 5 by molten steel S1-S3 fluid origin steel band G respectively and heat in heater 5 with temperature promote Δ T reach each hot rolling initial temperature WAT and in rolling-mill housing 9 with three passages with total deformation degreeThe hot rolled strip W with thickness d WB it is rolled into respectively with hot rolling final temperature WET。And then with cooldown rate tk, hot rolled strip W being cooled to each spooling temperature HAT respectively, steel band becomes coiled material C with this temperature spooling respectively。The parameters Δ T that provides respectively in the process to the steel band G cast by steel S1-S3, WAT, WET,DW, tk and HAT provide in table 2。
The hot rolled strip being made up of steel S3 processes with 1100 DEG C of hot band anneal carrying out 120s extraly after spooling in continuous annealing furnace。Although the hot rolled strip being made up of steel S3 has very high C, Mn and Al content, but can reliably avoid surface defect by this way。
Form 3 gives and is made up of steel S1-S3, through the structurally and mechanically character hot rolled strip thickness d WB of hot rolled strip, density p WB, extension limit Rp0.2, hot strength Rm, elongation percentage A80, n value and r value that above-mentioned the method according to the invention obtains。
| Steel | C | Mn | Al | Σ other |
| S1 | 0.55 | 18.0 | 6.0 | ≤0.14 |
| S2 | 0.75 | 24.0 | 9.0 | ≤0.09 |
| S3 | 1.25 | 26.0 | 11.5 | ≤0.15 |
Parameter provides with weight %, and surplus is ferrum and inevitable impurity。
Form 1
Form 2
N.e.=does not determine
Form 3
Claims (15)
1. the method manufacturing hot rolled steel sheet product, described method comprises the steps of
-molten steel (S) is melted, described molten steel is except ferrum and inevitable impurity are possibly together with (weight %)
C:0.5-1.3%,
Mn:18-26%,
Al:5.9-11.5%,
Si:0.1-0.4%,
Cr: less than 8%,
Ni: less than 3%,
Mo: less than 2%,
N: less than 0.1%,
B: less than 0.1%,
Cu: less than 5%,
Nb: less than 1%,
Ti: less than 1%,
V: less than 1%,
Ca: less than 0.05%,
Zr: less than 0.1%,
P: less than 0.04%,
S: less than 0.04%；
-described molten steel (S) is cast into the steel band (G) being cast；
-with the rate of heat addition of at least 20K/s, the described steel band (G) being cast is heated to the hot rolling initial temperature of 1100-1300 DEG C；
-the steel band (G) that would be heated to be cast described in hot rolling initial temperature is rolled into hot rolled strip (W)；
Start in-10s after hot rolling, with the cooldown rate of at least 100K/s, described hot rolled strip (W) is cooled to < 400 DEG C；
-at the spooling temperature less than 400 DEG C, cooled described hot rolled strip (W) spooling is become coiled material (C)。
2. method according to claim 1, it is characterized in that, described molten steel contains the Cr of (weight %) < 3.0%, the Ni of < 1.0%, the Mo of < 0.5%, the N of 0.005-0.04%, the B of < 0.0050%, the Cu of < 1%, the Nb of < 0.2%, the Ti of < 0.3%, the V of < 0.3%, the Ca of < 0.005%, the Zr of < 0.005%, the S of P or 0.005-0.02% of 0.01-0.03%。
3. method according to claim 1, it is characterised in that roll the steel band (G) implementing will to be cast described in described molten steel casting one-tenth in casting machine in two steps。
4. method according to claim 1, it is characterised in that described in the thickness of steel band (G) that is cast be 5mm to the maximum。
5. method according to claim 1, it is characterised in that the heater (5) by induction mode work is implemented to be heated to hot rolling initial temperature post。
6. method according to claim 1, it is characterised in that the heating of the described steel band (G) being cast is reached to be at least the hot rolling initial temperature of 1150 DEG C。
7. method according to claim 1, it is characterised in that the total deformation degree that realizes in the hot rolling is minimum is 10%。
8. method according to claim 7, it is characterised in that the total deformation degree realized in the hot rolling is 10-20%。
9. method according to claim 1, it is characterised in that the hot rolling final temperature of course of hot rolling is 1000-1050 DEG C。
10. method according to claim 1, it is characterised in that described course of hot rolling is implemented in a rolling pass。
11. method according to claim 1, it is characterised in that proceed by the cooling of the acceleration of described hot rolled strip (W) in the 10s after described course of hot rolling terminates。
12. method according to claim 1, it is characterised in that implement the step before hot rolling processes of described method under protective gas atmosphere (A)。
13. method according to claim 1, it is characterised in that described hot rolled strip (W) is carried out the hot band anneal under the annealing temperature of 900-1150 DEG C and processes。
14. method according to claim 13, it is characterised in that described in the Al content of steel band (G) that is cast be at least 10 weight %。
15. the method described in any one according to aforementioned claim, it is characterised in that described hot rolled strip (W) is cold rolled to cold-rolled strip。
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102011000089A DE102011000089A1 (en) | 2011-01-11 | 2011-01-11 | Method for producing a hot rolled flat steel product |
| DE102011000089.5 | 2011-01-11 | ||
| PCT/EP2011/072671 WO2012095232A1 (en) | 2011-01-11 | 2011-12-14 | Method for producing a hot-rolled flat steel product |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103328120A CN103328120A (en) | 2013-09-25 |
| CN103328120B true CN103328120B (en) | 2016-06-22 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201180064797.6A Expired - Fee Related CN103328120B (en) | 2011-01-11 | 2011-12-14 | The method manufacturing hot rolled steel plate product |
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| Country | Link |
|---|---|
| US (1) | US20140007992A1 (en) |
| EP (1) | EP2663411B1 (en) |
| JP (1) | JP2014505172A (en) |
| KR (1) | KR20130100215A (en) |
| CN (1) | CN103328120B (en) |
| BR (1) | BR112013017753A2 (en) |
| CA (1) | CA2823095C (en) |
| DE (1) | DE102011000089A1 (en) |
| ES (1) | ES2625281T3 (en) |
| MX (1) | MX345374B (en) |
| RU (1) | RU2554265C2 (en) |
| WO (1) | WO2012095232A1 (en) |
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- 2011-12-14 KR KR1020137021027A patent/KR20130100215A/en active Search and Examination
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Also Published As
| Publication number | Publication date |
|---|---|
| ES2625281T3 (en) | 2017-07-19 |
| MX345374B (en) | 2017-01-26 |
| DE102011000089A1 (en) | 2012-07-12 |
| BR112013017753A2 (en) | 2016-10-11 |
| WO2012095232A1 (en) | 2012-07-19 |
| CN103328120A (en) | 2013-09-25 |
| CA2823095A1 (en) | 2012-07-19 |
| JP2014505172A (en) | 2014-02-27 |
| EP2663411A1 (en) | 2013-11-20 |
| US20140007992A1 (en) | 2014-01-09 |
| RU2013137456A (en) | 2015-02-20 |
| EP2663411B1 (en) | 2017-02-15 |
| CA2823095C (en) | 2015-09-08 |
| MX2013007874A (en) | 2013-07-29 |
| KR20130100215A (en) | 2013-09-09 |
| RU2554265C2 (en) | 2015-06-27 |
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