CN102439179A - Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product - Google Patents
Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product Download PDFInfo
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- CN102439179A CN102439179A CN2010800207539A CN201080020753A CN102439179A CN 102439179 A CN102439179 A CN 102439179A CN 2010800207539 A CN2010800207539 A CN 2010800207539A CN 201080020753 A CN201080020753 A CN 201080020753A CN 102439179 A CN102439179 A CN 102439179A
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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
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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
- 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
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
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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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Abstract
The invention relates to a method for manufacturing a hot-rolled steel strip product with a thickness of 2 - 12 mm from low-alloy steel having a carbon content of 0.04 - 0.08 in percentage by weight and containing niobium and titanium. In order to obtain good mechanical properties, with bending properties included, for the steel strip product, a work piece of steel is austenized at an austenizing temperature of 1200 - 1350 DEG C, the steel work piece is hot-rolled at a pre-rolling step, the pre-rolled steel work piece is rolled in a strip roll mill so that a rolling temperature of 760 - 960 DEG C is achieved for the work piece in the last pass, and the steel strip is direct quenched after the last pass in the strip roll mill by a single-step cooling at a cooling rate of 30 - 150 DEG C/s to a temperature of 300 DEG C at the most, the direct quenching being carried out within 15s from the last pass. The invention also relates to a steel strip product.
Description
Background technology
The present invention relates to a kind of method of utilizing steel manufacturing to have the hot rolled strip product of 2 to 12mm wall thickness, the composition of said steel is by weight percentage:
C：0.04-0.08
Si：0-0.5
Mn：1-2.2
Nb：0.04-0.09
Ti：0.06-0.16
N：＜0.01
P：≤0.03
S：＜0.015
Al：0.01-0.15
V：≤0.1
Cr：＜0.2
Mo：＜0.2
Cu：≤0.5
Ni：≤0.5
And remaining iron and unavoidable impurities.Low carbon content is fabulous for offering the good welding characteristic of steel.The low-carbon-equivalent of steel also has positive effect for good weldableness.
The invention further relates to and have 2 to the 12mm wall thickness and the as above product made from steel of described composition.
EP 1319725 has disclosed the method that is used to make the steel band with top composition.The intensity of the steel band of making thus is higher, and its ys surpasses 690MPa, and after fracture, has higher elongation (12 to 21%).According to this publication, these mechanical propertys reach through steel being carried out the cooling of two steps.In first cooling step; Carrying out very fast cooling, surpass 150 ℃/second in hot rolling postcooling speed, then is not have initiatively 3 to 10 seconds time-out of refrigerative; Thereafter carry out the coiling temperature of second cooling step to steel band to be made, said temperature is selected according to desired intensity.The coiling temperature of recommendation that is used for surpassing the ys of 690MPa is 580 ℃.The high rate of cooling above 150 ℃/second when the first quenching step only can obtain when hanging down tape thickness, and this publication has only been discussed the tape thickness that is lower than 4mm.The cooling time-out means the phase change time that provides, and compares with continuing cooling therebetween, and said YIELD STRENGTH especially reduces, and ys/tensile strength values reduces.This publication does not disclose when coiling temperature is lower than 580 ℃, in steel, how to obtain to surpass the ys of 690MPa.This publication is illustrated in the ys that obtains in the coiling temperature that is lower than 580 ℃ and still is lower than 690MPa.
Said two steps cooling is implemented more complicated than step cooling in practice, and needs more complicated production unit.In addition, the toughness that cools off the steel band that obtains through two steps is not good especially, though said steel band has value preferably aspect the post-rift elongation.Toughness is meant that steel band bends to little bending radius and does not occur the ability of surface disturbance at the point of inflection place.It successfully is that steel provides good especially impact value and HS when low temperature that the cooling of two steps does not have.
Summary of the invention
The objective of the invention is to overcome the said shortcoming of prior art and provide for the belt steel product (being generally steel band) of making HS and the good especially toughness method of enforcement easily, said belt steel product has chemical constitution as mentioned above.In order to realize this purpose, being characterized as of method of the present invention:
-the workpiece of austenitizing steel under 1200-1350 ℃ austenitizing temperature;
-in advance-rolling step in the said steel workpiece of hot rolling system;
-in strip mill (strip rolling mill) rolling said in advance-rolling steel workpiece so that in the end realize being used for 760-960 ℃ rolling temperature of said workpiece in the passage (last last pass); And
-in said strip mill behind said final pass; Through one step cooling with said steel band with 30-150 ℃/second rate of cooling direct quenching to the highest 300 ℃, parallel extinguishing (parallel extinction) carried out in 15 seconds at said final pass.
The present invention shows astoundingly: said steel is formed can produce the plow-steel that also has good toughness.Also surprisingly, the intensity of also finding said steel is isotropic, that is, no matter with respect to the vertically still cross measures of said rolling direction, its ys does not have noticeable change.
Preferably at the most 120 ℃/second of said direct quenching speed, because this can obtain to provide for steel the steel microstructure of special favorable mechanical performance, said mechanical property comprises good shock strength and good toughness.
Preferably at the most 100 ℃ of outlet temperatures in the direct quenching because this can obtain after quenching, to have the plane with in addition the flat strip (smooth steel band) at edge.
Said steel band is preferably directly batched to coiling temperature and quilt by direct quenching.
The processing of said steel band is preferably deformation heat (heat machinery), therefore after direct quenching, does not carry out tempering.Though observed the tempering that on product, need not increase cost, had the favorable mechanical performance with the product made from steel of said method manufacturing.Tempering does not significantly improve mechanical performance of products, and it makes said process complicated.
Preferred implementation of the present invention discloses in accompanying claims 2-6.
The major advantage of method of the present invention is that it allows to have the favorable mechanical performance, and the product made from steel that comprises toughness and predetermined composition are with simple and economic mode and use simple device fabrication.
The invention further relates to the product of in method steps of the present invention, making.
Steel band product of the present invention has the wall thickness of 2-12mm, and is made up of following by weight percentage:
C：0.04-0.08
Si：0-0.5
Mn：1-2.2
Nb：0.04-0.09
Ti：0.06-0.16
N：＜0.01
P：≤0.03
S：＜0.015
Al：0.01-0.15
V：≤0.1
Cr：＜0.2
Mo：＜0.2
Cu：≤0.5
Ni：≤0.5，
All the other are iron and unavoidable impurities; The microstructure that it is characterized in that said steel is low-carbon (LC) ferritic and/or low-carbon bainite basically; Said steel is kept the bending radius of R≤0.75t and is not had macroscopic crack or crackle after bending; T is the thickness of said product made from steel, and its ys is 650-800MPa, and its elongation of fracture back is at least 12%.
Obtained HS, however the microstructure of said steel mainly form by low-carbon (LC) ferritic and/or bainite, and do not comprise the rich carbonaceous martensite or the rich carbonaceous bainite of significant quantity.Like what recommend, principal phase is made up of like a spot of bainite and/or martensite in the minimum island that recommend and enriched with carbon content and/or remaining austenite the microstructural ferritic of ferritic that has almost completely.For the high-intensity remarkable reason that obtains is in the steel of producing with present method, to use niobium and titanium as microalloy element.Must use niobium and titanium.
Preferred implementation of the present invention is disclosed among the appended claim 8-19.
The major advantage of product made from steel of the present invention is with respect to its composition, and its favorable mechanical performance comprises toughness and shear property and impact value.Said steel also is applicable in the cold conditions (arctic condition) fully.Steel of the present invention is because its performance relevant with engineering work is very useful, because its toughness is good, and its isotropic strength property allows the very effective optimization of its use.In addition, little bending radius is convenient to bent products planner's work especially.Steel band product of the present invention is especially suitable for use as strong structure iron.
Description of drawings
To disclose the present invention in more detail and with reference to accompanying drawing below, wherein:
Fig. 1 shows method steps of the present invention;
Fig. 2 is the crooked synoptic diagram of V-in the crooked test;
Fig. 3 shows the instance of the bend test results of success;
Fig. 4 shows the instance of the bend test results of failure;
Fig. 5 representes the transition curve with the but shellfish-V (charpy-V) of steel of the present invention and reference steel acquisition;
Fig. 6 shows related between ys isotropy and the strip-rolling; And
Fig. 7 shows related between ys isotropy and the coiling temperature.
Embodiment
Fig. 1 shows to be used to produce has 2 method stepss of the present invention to the steel band product of 12mm wall thickness.Said manufacturing begins from the workpiece of steel, and its composition is by weight percentage:
C：0.04-0.08
Si：0-0.5
Mn：1-2.2
Nb：0.04-0.09
Ti：0.06-0.16
N：＜0.01
P≤0.03
S：＜0.015
Al：0.01-0.15
V：≤0.1
Cr：＜0.2
Mo：＜0.2
Cu：≤0.5
Ni：≤0.5
And remaining iron and unavoidable impurities.
Said steel has 0.04 to 0.08% low carbon content C, and its shock strength, toughness and weldableness of considering said material is favourable.
Silicon, Si can use as reductor (killing agent) (except aluminium) and be used for ferritic and strengthen (toughener) with 0 to 0.50% amount.If purpose is special favorable surface quality, then silicone content must be constrained to and be lower than 0.25%.
Manganese, the alloy content of Mn are 1.0 to 2.2%.Because low carbon content, so steel is not inclined to manganese and carbon segregation during casting, it has also improved microstructural homogeneity at the high level place of Mn.Preferably, at least 1.3% manganese by alloying to realize HS and to guarantee 2.0% weldableness at the most.
Steel of the present invention can be cut into the part (steel part, sheet) of precise measure through heat (for example, through laser and plasma body) and machinery.Observe, obtained to have the part on more level and smooth cutting surface.This has favorable influence for fatigue strength.In addition, the cutting surface became coarse during low carbon content had prevented thermal cutting, and had reduced highest hardness, and the cutting surface is being not easy to become fragile and crack during the formation of part He under its application conditions.In cut mechanically, cutting gap can be set to the value of the 10-15% of steel thickness, and cleaved products (result) remains level and smooth and non-cracking; Therefore; The grinding that separates or the thermal cutting on cutting surface are optional, its reduced significantly machining tolerance (performance tolerance, allowances); And reduced the quantity of manufacturing step, improved manufacturing processed thus.
In order to realize good shock strength and toughness, as the phosphorus that impurity exists, the amount of P (at the most 0.03%) and sulphur, the amount of S (at the most 0.015%) is limited.The maximum of P is preferably 0.015%, and the maximum of S is preferably 0.005%.In addition, where necessary, handle, can improve performance through Ca or CaSi with fusing.As reductor, used aluminium Al 0.01-0.15%.The amount of the aluminium that uses is preferably at the most 0.05%.
The nitrogen that uses, the amount of N is at the most 0.01%, because when in titaniferous steel, exist, the hard titanium nitride particles of the toughness of nitrogen formation weakening steel.The preferred amounts of the nitrogen that uses is at the most 0.006%.
Copper, the content of Cu are reduced at the most 0.3%, to guarantee the favorable surface quality of hot rolling band.If copper content surpasses 0.3%, recommend also alloying (fusion) to equal the nickel of 0.25 times amount of Cu content, Ni at least.Though steel ought it can be used, to gain in strength a little not having also to have realized the performance that it is good under the situation of copper in case of necessity.Cu content is at the most 0.5%.Especially for for example 8 to 12mm thick band, preferably use the copper of alloy 0.3-0.5% and at least 0.1% nickel.
Even do not have copper in the said alloy, Ni also is restricted at the most 0.5%.Though steel has also been realized the strength property that it is good when not mixing Ni, in case of necessity, it can be gained in strength a little.
Boron, B is not fully by alloying (fusion), because it will unnecessarily increase sclerosis.Therefore the boron content in the steel band product of the present invention is restricted to impurity level, i.e. B＜0.0005%.
Titanium, T can be by alloying (fusion) to realize the desired intensity level.Typically be 0.06-0.16%, though higher Ti level also can be used, under said situation its intensity increase effect minimum, and can make the casting of workpiece complicated.Lower Ti per-cent is not used, because like this, does not use more expensive alloying or increase carbon content just to be difficult to obtain HS to surpassing 0.08%.It is shocking, even it is the present invention shows that at low temperature under-40 ℃ and-60 ℃, titanium also reduces the shock strength of basic reagent indistinctively, shown like measuring result through table 3.
Chromium, Cr, and molybdenum, Mo need be by alloying (fusion).They are the elements that increase sclerosis and when higher amount, weldableness is had disadvantageous effect at least.For this reason, Cr is restricted to 0.2% maximum level, and similarly, Mo is restricted to 0.2% maximum level.The amount of chromium is preferably less than 0.1%.
Molybdenum preferably is allowed to 0.10% amount at the most, and 0.5% amount at the most most preferably is because the mechanical property of steel of the present invention provides the titanium of the alloying element cost that more can afford than molybdenum through alloying (fusion) and realized by override.Molybdenum in the steel band product of direct quenching of the present invention for intensity even possibly be deleterious.In any situation, when product was produced through thermomechanical treatment, the molybdenum of adding also improved the intensity of steel band product of the present invention indistinctively.
Vanadium, V need be by alloying (fusion).In addition, it has increased unnecessary sclerosis, and under high density, has disadvantageous effect for weldableness at least.For this reason, V is restricted to 0.1% maximum level.
Yet; Especially to having 2 to the low strap thickness t of 6mm, when high rolling load, in order to reduce rolling load; Nb and Ti concentration are limited as follows: Nb:0.04-0.06% and Ti:0.06-0.10%, the vanadium concentration V that can select 0.06-0.10% simultaneously is to obtain HS.
For low strap thickness t=2-6mm, silicon also can be advantageously be added into the amount of Si:0.30-0.50%, gaining in strength, shown in the table 1 of the test carried out with experimental group compound (composition) E1.
According to preferred implementation of the present invention, the summation of niobium, titanium and vanadium concentration is greater than 0.15%, that is, Ti+Nb+V＞0.15%, the steel band product is used as strong especially structure iron.
Especially when lower carbon content restriction, steel band product of the present invention is fabulous aspect crooked (backfin) and welding, as, be welded in pipe or the pipe fine strain of millet through automatic high frequency (HF).Make experiment and shown that said material is very suitable for producing the pipe fine strain of millet of HF-welding.
The workpiece of steel is that 210mm is thick, for example, and is heated to 1280 ℃ austenitizing temperature, it is kept about 3 hours here.Certainly, the thickness of steel workpiece can be different from here the thickness that discloses, and austenitizing temperature can be selected differently, but recommends 1200-1350 ℃ scope.If austenitizing temperature is lower than the lower limit that provides, then have such risk: micro alloying element can not dissolve in austenite,, can not obtain the austenite of homogeneous that is.Most preferably, annealing time changes in 2-4 hour scope.
The carbon equivalent C+Mn/6+ of steel (Cr+Mo+V)/5+Ni+Cu)/15 preferably is not higher than 0.45, and it has guaranteed the good welds property of steel.
Behind austenitizing, steel workpiece under 950-1250 ℃ temperature by hot rolling to the thickness that is generally 25-50mm, transferred to strip mill subsequently immediately to be rolled into the band of final thickness with 2-12mm.The final thickness of the recommendation of steel band is 4mm at least.Also recommend final thickness to be no more than 10mm.
The quantity of passage is generally 5 to 7 in the strip mill.Final pass in the strip mill is implemented at 760-960 ℃ TR place, is recommended as 780-850 ℃.
In the end after the passage, the direct quenching of steel band began in 15 seconds.At the place that begins of direct quenching, the temperature of steel band is necessary at least 700 ℃.Direct quenching is implemented with 30-150 ℃/second quench rates as water quenching, is limited to 120 ℃/second at the most in the recommendation.Direct quenching continues up to 300 ℃ temperature at the most, and the temperature of recommendation is 100 ℃.After the direct quenching, steel is batched immediately.Therefore, coiling temperature can fall in 30-300 ℃ the TR.The initial coiling temperature of recommending be 100 ℃ at the most because when steel when being batched above quilt under 100 ℃ the temperature, the complicated discontinuous steam cushion of said process can be formed on the steel surface.
As the result of thermomechanical treatment, the microstructure of steel becomes evenly, and is made up of mutually leading, and it is preferably low-carbon (LC) ferritic and/or low-carbon bainite.The amount of leading phase surpasses 90% usually.In other words, the upper bainite of extremely low amount and/or residual austenite and/or martensite exist in high carbon group.Average grain size in the microstructure (granularity) is less, is preferably about 2-4 micron.Also necessary is that said microstructure does not at first comprise big crystal grain, therefore, considers the intensity of steel, and said steel has good especially curved characteristic.Grain-size is homogeneous and meticulous as far as possible, and it is realized through method of the present invention.
Below table 1 to 3 steel of the present invention is provided concentration and Fabrication parameter instance and utilize the intensity of their acquisitions and the instance of toughness value.In order to compare, table 2 and 3 also comprises the Fabrication parameter of the scope that does not belong to method of the present invention,, does not correspond to the processing of method of the present invention that is.In table 2,, and in table, illustrate with reference to test with R for mechanical strength properties for Fabrication parameter.
The curved characteristic that other the theming as that detects utilizes processing of the present invention to obtain; These compare with the curved characteristic that obtains through the Fabrication parameter outside the scope of the present invention; Referring to table 3 and 4, steel B3Q23 (a)) and steel A3M33 (the crooked test b outside the present invention) according to crooked test of the present invention).
Temperature when the index T_f in the table 2 representes last rolling pass, the temperature when index T_c representes to batch beginning, index Th representes the thickness of steel band, and index Wi representes the width of steel band.
Table 3 first row in, T representes such sample, its intensity and toughness cross on the direction of take-up direction determined.Terminal (ending) L representes such sample, and its intensity and toughness are determined on take-up direction.
(subject composition) formed in table 1. test
| Analyze | C | SI | MN | P | S | AL | NB | V | CU | CR | NI | N | MO | TI | CA | Ti+Nb+V | Embodiment |
| A1 | 0.049 | 0.23 | 1.99 | 0.008 | 0.003 | 0.03 | 0.08 | 0.01 | 0.03 | 0.04 | 0.04 | 0.005 | 0.10 | 0.20 | 1.2.3 | ||
| A2 | 0.049 | 0.19 | 1.92 | 0.007 | 0.003 | 0.03 | 0.09 | 0.01 | 0.04 | 0.04 | 0.05 | 0.005 | 0.01 | 0.10 | 0.003 | 0.19 | 10 |
| A3 | 0.049 | 0.19 | 1.89 | 0.009 | 0.002 | 0.03 | 0.08 | 0.01 | 0.01 | 0.03 | 0.05 | 0.005 | 0.00 | 0.10 | 0.003 | 0.19 | 9 |
| B2 | 0.056 | 0.21 | 1.81 | 0.007 | 0.003 | 0.03 | 0.09 | 0.01 | 0.04 | 0.04 | 0.05 | 0.007 | 0.01 | 0.11 | 0.003 | 0.21 | 5 |
| B3 | 0.056 | 0.21 | 1.76 | 0.008 | 0.004 | 0.03 | 0.08 | 0.01 | 0.03 | 0.04 | 0.05 | 0.004 | 0.01 | 0.11 | 0.002 | 0.19 | 6.9 |
| B4 | 0.064 | 0.21 | 1.78 | 0.011 | 0.001 | 0.03 | 0.09 | 0.01 | 0.04 | 0.06 | 0.06 | 0.009 | 0.01 | 0.11 | 0.003 | 0.20 | 4.10 |
| C1 | 0.053 | 0.18 | 1.78 | 0.008 | 0.004 | 0.03 | 0.06 | 0.00 | 0.03 | 0.05 | 0.05 | 0.008 | 0.01 | 0.14 | 0.003 | 0.19 | 8 |
| D1 | 0.057 | 0.17 | 1.65 | 0.008 | 0.003 | 0.03 | 0.04 | 0.01 | 0.03 | 0.03 | 0.04 | 0.005 | 0.09 | 0.14 | 7 | ||
| E1 | 0.079 | 0.39 | 1.43 | 0.011 | 0.003 | 0.03 | 0.05 | 0.08 | 0.04 | 0.06 | 0.06 | 0.007 | 0.01 | 0.06 | 0.002 | 0.20 | 11 |
| F1 | 0.061 | 0.23 | 1.79 | 0.008 | 0.001 | 0.04 | 0.08 | 0.01 | 0.40 | 0.07 | 0.20 | 0.007 | 0.01 | 0.12 | 0.002 | 0.22 | 12 |
| F2 | 0.058 | 0.20 | 1.90 | 0.007 | 0.002 | 0.03 | 0.08 | 0.01 | 0.40 | 0.06 | 0.21 | 0.006 | 0.02 | 0.12 | 0.002 | 0.21 | 12 |
| B5 | 0.06 | 0.21 | 1.81 | 0.009 | 0.004 | 0.03 | 0.08 | 0.01 | 0.04 | 0.07 | 0.08 | 0.007 | 0.02 | 0.11 | 0.002 | 0.20 |
Table 2. Fabrication parameter
| Sample | T_f | T_c | Th | Wi | Embodiment | ||
| A1M33 | 875 | 605 | 5 | 1260 | 1 | R | |
| A1M63 | 905 | 480 | 5 | 1260 | | R | |
| A1Q61 | |||||||
| 920 | 250 | 5 | 1260 | 2b | |||
| A1M83 | 885 | 50 | 5 | 1260 | 3 | ||
| B2L13 | 910 | 360 | 10 | 1260 | 5 | R | |
| B3Q25 | 805 | 50 | 10 | 1270 | 6 | ||
| D1Q63 | 865 | 50 | 5 | 1500 | 7 | ||
| C1Q35 | 910 | 50 | 7.7 | 1355 | 8 | ||
| A3M33 | 890 | 615 | 10 | 1520 | 9 | R | Crooked b |
| B3Q23 | 830 | 50 | 10 | 1270 | 9 | Crooked a | |
| A2M33 | 895 | 605 | 8 | 1330 | 10 | R | Transition curve 9c |
| B4Q23 | 835 | 50 | 8 | 1500 | 4.10 | Transition curve 9d | |
| E1Q11 | 825 | 50 | 6 | 1500 | 11 | ||
| E1Q33 | 860 | 50 | 5 | 1500 | 11 |
| Sample | T_f | T_c | Th | Wi | Embodiment | ||
| F1Q23 | 810 | 50 | 12 | 1500 | 12 | ||
| F2Q43 | 805 | 50 | 12 | 1250 | 12 | ||
| B5Q23 | 820 | 50 | 6 | 1500 | Crooked c |
Table 3. intensity and toughness properties
Table 2 and 3 shows that impact value is good, and intensity is isotropically high when direct quenching is implemented into low temperature (50 ℃).
Like what see, be 635-829MPa according to the ys of steel of the present invention from table 3.Post-rift elongation A5 is at least 12%, is generally at least 15%.The yield tensile ratio of steel (ys/breaking tenacity) is about 0.8-0.95.
Can further reach a conclusion from the result of table 1 to 3: embodiment 3,4,6,7,9,11 and 12, the yield strength value of the steel band on the machine direction of steel band and the cross-machine direction is also inapparent each other different.Ys on the machine direction almost with cross-machine direction on ys the same high, the ratio of intensity is＜6.5%, even＜2%.According to embodiment, low like this Strength Changes is to implement to be quenched into the temperature that is lower than 100 ℃ and/or through utilizing 890 ℃ final strip-rolling temperature to obtain through preferred implementation according to the present invention.
Shown in table 2 and 3, said homogeneous quality is present in wherein final rolling temperature lower (being lower than 890 ℃) and/or batches in the steel of (50 ℃ of coiling temperatures) at low temperature.
Reference value from table shows that for embodiment 1,2a and 5, when coiling temperature surpassed 100 ℃, the isotropy of hardness of steel value was reduced to the value near 10%, and this representative is for the common variation of the intensity level of steel routine, that deformation heat is produced.This is equally applicable to the breaking tenacity value.
Final flexure temperature T_f and coiling temperature T_c check isotropic the acting in Fig. 6 and 7 of ys in more detail, and it shows that the reduction of final flexure temperature and coiling temperature allows the ys of steel of the present invention to be enhanced.
The present invention also show the ys isotropy can utilize formula Rp (T-L)/Rp (L)=-46.6+0.0576T_f+0.0103T_c assesses, wherein T_f is final flexure temperature, and T_c is a coiling temperature.
The homogeneous quality is favourable, because when the steel band that is used for various objectives is designed, need not consider such fact, that is, said steel band has higher intensity on than the direction of crossing take-up direction on the take-up direction.Therefore, in all situation, that is, also when cutting is processed to the blank of product (it in use accepts their maximum load on the direction corresponding to the take-up direction of steel band) can be utilized the HS of steel band.In addition, the use of steel band can be optimised, because need not be considered about the Strength Changes of loading direction.In addition, the isotropic intensive property has the formation of the bending of the homogeneous quality that helps not consider bending direction (vertically/laterally), and it has further improved the suitability of steel band product of the present invention.Table 4 shows that the toughness (it is known to be problematic) in the longitudinal bending is fabulous.For example, steel sample B5Q3 allows to reach 1.3 R/T value in longitudinal bending.The cross bow of this steel still successfully reaches 0.3 R7t value.
The crooked art methods of having passed through is implemented as the V-between the instrument of upper and lower is crooked, and Fig. 3 shows principle.Used bending method is the free bend with V-A/F V of 100mm.Test block is bent on both direction, and they are curved Z-shaped thus.
The crooked result of table 4..Square plate with the side length with 300-400mm is crooked, and the bending of carrying out intersects with rolling direction.In table, R represents bending radius, and t represents sheet gauge.Crooked test and rolling direction laterally (T) are carried out.
The result of crooked test is visually analyzed.Fig. 3 shows the bending (good) of the success with circular bending shape and full surface.Underproof result (failure) is owing to visible crackle, slight crack or corner angle in the zone of bending radius cause.Table 5 shows the typical crooked mistake that causes defective result, and table 4 shows the instance of the bending (failure) of obvious failure.
The typical bending defect of table 5. (lost efficacy, faults) by failure
Title is described
| Edge crack | Edge crack on the sheared edge of outside sweep |
| Very thin surface crack | Visible yield line in the bending |
| Thin surface crack | The yield line that shows as groove clearly |
| (surface crack) | Possible crackle on the curved surface |
| Surface crack | The crackle that reflects on the curved surface |
| Open crackle | Clearly fracture on the curved surface |
As shown in Figure 4, (crooked test in the table 2 a) has a much better toughness than steel A3M33 (the crooked test b in the table 2) to steel B3Q23.In steel of the present invention, the ratio of the bending radius and the strength of materials (R/t) can even be 0.4, and the ratio that the reference steel through the routine manufacturing reaches is merely about 1.6.From table 1 to 4 with Fig. 5 the conclusion that draws be in the method for the invention, direct quenching is proceeded to 300 ℃ temperature at the most.
Shown in table 3 and Fig. 5, the impact value that obtains from steel sample B4Q23 (transition curve d) is significantly good than the impact value that obtains from steel sample A2M33 (transition curve c).The steel sample of front is by the temperature (with reference to table 2) of direct quenching to 50 ℃, and the latter is cooled to 615 ℃ temperature.Table 3 shows that also being cooled to about 600 ℃ high temperature (embodiment 1 and 10) only causes for the typical impact value of the steel of this intensity rank.As shown, under-20 ℃ temperature, the shock strength of steel of the present invention is 200J/cm at least
2, and/or under-40 ℃ temperature, be 190J/cm at least
2, and/or under-60 ℃ temperature, be 180J/cm at least
2
At last, the present invention will explain through describing test implementation example and table 1 to the information in 4 in more detail.
Embodiment 1.Strip mill is used to the hot steel band of the thickness of the rolling 5mm of having and the composition of table 1 (A1).Rolling parameter (A1M33) is shown in the table 2.Result (A1M33) is shown in the table 3.The result shows, when steel band is batched under 600 ℃ coiling temperature, realize fabulous intensity, but shock strength is still only at normal level.Noticeable aspect is that ys is obviously different on different measurement directions, and its micro-alloyed steel for the hot pair rolling of deformation is normal.The elongation level is normal.
Embodiment 2.Strip mill is used to the hot steel band of the thickness of the rolling 5mm of having and the composition of table 1 (A1).Rolling parameter (A1M63) is shown in the table 2.The result is shown in the table 3.But the result shows, under low coiling temperature (about 480 ℃), batches the steel (A1M63) of the impact energy that produces low strength improve.The elongation level is normal.Said band is cooled to the intensity (approaching normal level) that still lower cooling temperature (about 250 ℃) has improved steel (A1Q61), has wherein obviously improved impact energy.Elongation still is lower than normal level.
Embodiment 3.Strip mill is used to the hot steel band of the thickness of the rolling 5mm of having and the composition of table 1 (A1).Rolling parameter (A1M83) is shown in the table 2.Result (A1M83) is shown in the table 3.The result shows that batching under low-down coiling temperature (about 50 ℃) brings up to intensity near normal good level, and wherein impact energy still obviously is better than normal level.Elongation still is lower than normal level.
Embodiment 4.Strip mill is used to the hot steel band of the thickness of the rolling 8mm of having and the composition of table 1 (B4).Rolling parameter (B4Q23) is shown in the table 2, and corresponding results is shown in the table 3.The result shows that batching under low-down coiling temperature (about 50 ℃) brought up to normal level with intensity, and provides and obviously be better than normal impact energy.And, it should be noted that ys on the rolling direction on horizontal and vertical much at one.Elongation is a shade below normally.
Embodiment 5.Strip mill is used to the hot steel band of the thickness of the rolling 10mm of having and the composition of table 1 (B2).Rolling parameter (B2L13) is shown in the table 2, and corresponding results is shown in the table 3.The result shows, under very high rolling temperature (910 ℃) and batching under 360 ℃ coiling temperature, the vertical ys on the bending direction still is in low-level, but impact energy is still good.Elongation roughly is in normal level.
Embodiment 6.Strip mill is used to the hot steel band of the thickness of the rolling 10mm of having and the composition of table 1 (B3).Rolling parameter (B3Q25) is shown in the table 2, and corresponding results is shown in the table 3.The result shows that under low-down rolling temperature (about 800 ℃) and under the low-down coiling temperature (about 50 ℃), for thick band, ys is also brought up to normal level, and wherein shock strength still is in good level.Noticeable aspect is identical horizontal and vertical about the ys of rolling direction.Elongation is lower than normal level slightly.
Embodiment 7.Strip mill is used to the hot steel band of the thickness of the rolling 5mm of having and the composition of table 1 (D1).Rolling parameter (D1Q63) is shown in the table 2, and corresponding results is shown in the table 3.The result shows that when steel was quickly cooled to 50 ℃ temperature, the minimizing of alloying element (especially Ti, Nb) greatly reduced intensity.Elongation and shock strength are in good level.
Embodiment 8.Strip mill is used to the hot steel band of the thickness of the rolling 7.7mm of having and the composition of table 1 (C1), and said steel band is used to make square (quadratic) pipe fine strain of millet of the HF-welding of the size with 100mm * 250mm subsequently.Rolling parameter (C1Q35) is shown in the table 2, and the result who measures from pipe fine strain of millet is shown in the table 3.The intensity level of measuring is that pipe fine strain of millet forms the intensity that the back obtains.Because in the manufacturing of pipe fine strain of millet, cold shaping takes place, so impact value descends usually slightly.The result shows that the steel according to said method also is very suitable for making double-strength pipe fine strain of millet.
Embodiment 9.Strip mill is used to the hot steel band of the thickness of the rolling 8mm of having and the composition of table 1 (A3 and B4).Rolling parameter (A3M33 and B3Q23) is shown in the table 2, and the corresponding test result of measuring from said steel band is shown in the table 3.Table 4 shows the comparison of the bending of these steel (A3M33 and B3Q23), notices that thus the steel B3Q23 of direct quenching keeps crooked good at R/t value 0.4 place.The steel A3M33 that is cooled to about 600 ℃ temperature can successfully be bent to R/t value 1.6.
Embodiment 10.Fig. 5 has compared the impact value at steel A2M33 of different probe temperatures place and B4Q23 through but shellfish V shock test.The composition of steel A2M33 and B4Q23 and Fabrication parameter are shown in the table 1 and 2.The steel B4Q33 proof of direct quenching is obviously better also kept its intensity under extremely low temperature.
Embodiment 11.Strip mill be used to rolling have 5 with the hot steel band of the composition (E1) of the thickness of 6mm and table 1.Rolling parameter (E1Q11 and E1Q33) is shown in the table 2, and the corresponding test result of measuring from said steel band is shown in the table 3.The result shows that steel band product of the present invention also can be made in little thickness, for example, and through niobium, titanium and the content of vanadium of selecting following steel: Nb:0.04-0.06%, Ti:0.06-0.10%, and V:0.06-0.1%.
Embodiment 12.Strip mill is used to the hot steel band of the thickness of the rolling 12mm of having and the composition of table 1 (F1 and F2).Rolling parameter (F1Q23 and F2Q43) is shown in the table 2, and the corresponding test result of measuring from said steel band is shown in the table 3.The result shows that steel band product of the present invention also can be with thick size manufacturing.In addition, this embodiment further proof through being implemented into the temperature that is lower than 100 ℃ direct quenching and/or be lower than 890 ℃ strip-rolling outlet temperature through utilization and obtain the homogeneous quality.
Hereinbefore, the present invention has been described through embodiment.Because this it should be noted that details of the present invention can be implemented in every way within the scope of the appended claims.
Claims (19)
1. one kind through utilizing steel manufacturing to have the method for the hot rolled strip product of 2 to 12mm thickness, and the composition of said steel is by weight percentage:
C：0.04-0.08
Si：0-0.5
Mn：1-2.2
Nb：0.04-0.09
Ti：0.06-0.16
N：＜0.01
P：≤0.03
S：＜0.015
Al：0.01-0.15
V：≤0.1
Cr：＜0.2
Mo：＜0.2
Cu：≤0.5
Ni：≤0.5，
All the other are made up of iron and unavoidable impurities, it is characterized in that:
-the workpiece of austenitizing steel under 1200 to 1350 ℃ austenitizing temperature;
-said the steel workpiece of hot rolling system in preparatory rolling step;
-rolling said rolling steel workpiece in advance in strip mill makes in the end to reach 760 to 960 ℃ rolling temperature for said workpiece in the passage; And
-in said strip mill behind said final pass, through the one step cooling rate of cooling with 30 to 150 ℃/second, to 300 ℃ at the most, said direct quenching is being carried out in 15 seconds from said final pass with said steel band direct quenching.
2. method according to claim 1 is characterized in that, said direct quenching speed is 120 ℃/second at the most.
3. method according to claim 1 and 2 is characterized in that, the outlet temperature of said direct quenching is 100 ℃ at the most.
4. according to each described method in the aforementioned claim, it is characterized in that said steel band is directly batched to coiling temperature and quilt by direct quenching.
5. according to each described method in the aforementioned claim, it is characterized in that said steel band is not annealed after the direct quenching by thermomechanical treatment in this case.
6. according to each described method in the aforementioned claim, it is characterized in that said steel band is shaped as the pipe product after said direct quenching.
7. hot rolled strip product has the thickness of 2-12mm and following composition by weight percentage:
C：0.04-0.08
Si：0-0.5
Mn：1-2.2
Nb：0.04-0.09
Ti：0.06-0.16
N：＜0.01
P：≤0.03
S：＜0.015
Al：0.01-0.15
V：≤0.1
Cr：＜0.2
Mo：＜0.2
Cu：≤0.5
Ni：≤0.5，
All the other are iron and unavoidable impurities, it is characterized in that, the microstructure of said steel is low-carbon (LC) ferritic and/or low-carbon bainite basically,
The ys of said steel is 650-800MPa, and post-rift elongation is at least 12%; And
Said steel the ys on the said rolling direction with transverse to the ys on the direction of said rolling direction at the most under 6.5% condition of different, the structure of said steel is isotropic.
8. steel band product according to claim 7 is characterized in that, said ferritic of low-carbon (LC) basically and/or low-carbon bainite structure comprise the high-carbon island.
9. according to claim 7 or 8 described steel band products, it is characterized in that in cross bow, said steel is kept the bending radius of 0.4≤R≤0.75t, does not have macroscopic crackle or crack, wherein t is the wall thickness of said product made from steel.
10. according to each described steel band product in the aforementioned claim 7 to 9, it is characterized in that the average grain size of said steel band product is 2 to 4 microns.
11., it is characterized in that the carbon equivalent of said steel band product is at the most 0.45 according to each described steel band product in the aforementioned claim 7 to 10.
12., it is characterized in that the ys of said steel band product surpasses 680MPa according to each described steel band product in the aforementioned claim 7 to 11.
13., it is characterized in that the shock strength of said steel band product is 200J/cm at least according to each described steel band product in the aforementioned claim 7 to 12 under-20 ℃ temperature
2And/or under-40 ℃ temperature, be 190J/cm at least
2And/or under-60 ℃ temperature, be 180J/cm at least
2
14., it is characterized in that said steel band product can be cut at the cutting gap place of the 10-15% of sheet gauge and perceptible crackle visually not according to each described steel band product in the aforementioned claim 7 to 13.
15., it is characterized in that said steel is formed Ti+Nb+V＞0.15 that also meets the demands according to claim 7 or 8 described steel band products.
16. steel band product according to claim 15 is characterized in that, said steel band thickness of product is 2-6mm, and the content of said steel interalloy element nb, Ti and V is:
Nb：0.04-0.06
Ti：0.06-0.10
V：0.06-0.10。
17. steel band product according to claim 15 is characterized in that, the molybdenum content of said steel is Mo＜0.10.
18., it is characterized in that the molybdenum content of said steel is Mo＜0.05 according to claim 7 or 18 described steel band products.
19., it is characterized in that said steel band thickness of product surpasses 8mm, and the copper and mickel content of said steel is 0.3≤Cu≤0.5 and Ni＜0.1% according to claim 7 or 8 described steel band products.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
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| FI20095528A FI20095528A (en) | 2009-05-11 | 2009-05-11 | Process for producing a hot rolled strip steel product and hot rolled strip steel product |
| FI20095528 | 2009-05-11 | ||
| PCT/FI2010/050310 WO2010130871A1 (en) | 2009-05-11 | 2010-04-16 | Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product |
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| CN102439179A true CN102439179A (en) | 2012-05-02 |
| CN102439179B CN102439179B (en) | 2015-03-25 |
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| CN201080020753.9A Active CN102439179B (en) | 2009-05-11 | 2010-04-16 | Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product |
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| EP (1) | EP2430199B1 (en) |
| CN (1) | CN102439179B (en) |
| ES (1) | ES2738876T3 (en) |
| FI (1) | FI20095528A (en) |
| PL (1) | PL2430199T3 (en) |
| RU (1) | RU2535890C2 (en) |
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| Publication number | Publication date |
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| PL2430199T3 (en) | 2019-12-31 |
| RU2535890C2 (en) | 2014-12-20 |
| RU2011149763A (en) | 2013-06-20 |
| CN102439179B (en) | 2015-03-25 |
| EP2430199B1 (en) | 2019-05-29 |
| FI20095528A0 (en) | 2009-05-11 |
| EP2430199A1 (en) | 2012-03-21 |
| FI20095528A (en) | 2010-11-12 |
| ES2738876T3 (en) | 2020-01-27 |
| WO2010130871A1 (en) | 2010-11-18 |
| TR201910938T4 (en) | 2019-08-21 |
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