CN102439179B - 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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- CN102439179B CN102439179B CN201080020753.9A CN201080020753A CN102439179B CN 102439179 B CN102439179 B CN 102439179B CN 201080020753 A CN201080020753 A CN 201080020753A CN 102439179 B CN102439179 B CN 102439179B
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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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- Heat Treatment Of Sheet Steel (AREA)
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 utilizing steel to manufacture the hot rolled strip product with 2 to 12mm wall thickness, the composition of described 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 inevitable impurity.Low carbon content is fabulous for being supplied to the good welding characteristic of steel.The low-carbon-equivalent of steel also has positive effect for good weldability.
The invention further relates to and have 2 to 12mm wall thickness and the product made from steel formed as described above.
EP 1319725 discloses the method for the steel band for the manufacture of the composition had above.The intensity of the steel band manufactured thus is higher, and its yield strength more than 690MPa, and has higher elongation (12 to 21%) after fracture.According to this publication, these mechanical propertys reach by carrying out two step coolings to steel.In the first cooling step, carry out cooling quickly, rate of cooling is more than 150 DEG C/sec after hot rolling, is then the time-out of 3 to 10 seconds not having active cooling, thereafter carry out the coiling temperature of the second cooling step to steel band to be manufactured, described temperature is selected according to the intensity expected.Coiling temperature for the recommendation of the yield strength more than 690MPa is 580 DEG C.The high rate of cooling more than 150 DEG C/sec when the first quenching Step only can obtain when low tape thickness, and this publication only discusses the tape thickness lower than 4mm.Cooling time-out means provides the phase change time, and therebetween compared with lasting cooling, the yield strength of described material especially reduces, and yield strength/tensile strength values reduces.This publication does not disclose when coiling temperature is lower than 580 DEG C, how to obtain the yield strength more than 690MPa in steel.This publication shows that the yield strength obtained in lower than the coiling temperature of 580 DEG C is still lower than 690MPa.
Described two step coolings are implemented more complicated than a step cooling in practice, and need more complicated production unit.In addition, the bendability of the steel band obtained by two step coolings is not good especially, although described steel band has good value in post-rift elongation.Bendability refers to that steel band bends to little bending radius and do not occur the ability of surface damage at point of inflection place.Two steps coolings not successfully when low temperature for steel provides particularly preferred impact value and high strength.
Summary of the invention
The object of the invention is to overcome the described shortcoming of prior art and provide the method for the easy enforcement of the belt steel product (being generally steel band) manufacturing high strength and bendability good especially, described belt steel product has chemical constitution as mentioned above.In order to realize this object, the feature of method of the present invention is:
-under the austenitizing temperature of 1200-1350 DEG C the workpiece of austenitizing steel;
-in pre--milling step steel workpiece described in hot rolling;
The steel workpiece of-pre--rolling described in rolling in strip mill (strip rolling mill), so that in the end passage (last last pass) is middle realize the rolling temperature of 760-960 DEG C being used for described workpiece; And
-in described strip mill after described final pass, by one step cooling by described steel band with the rate of cooling direct quenching of 30-150 DEG C/sec to 300 DEG C at the most, described direct quenching is carrying out in 15 seconds from described final pass.
The present invention shows astoundingly: described steel composition can produce the high-strength steel also with good bendability.Also surprisingly, also find that the intensity of described steel is isotropic, that is, no matter relative to described rolling direction longitudinal direction or cross measures, its yield strength does not have noticeable change.
Described direct quenching speed preferably 120 DEG C/sec at the most, because this can obtain as steel provides the steel microstructure of mechanical property good especially, described mechanical property comprises good shock strength and good bendability.
Preferably, the outlet temperature of direct quenching is 100 DEG C at the most, because this can obtain the flat strip (smooth steel band) after quenching with plane and even edge.
Preferably, described steel band is directly arrived coiling temperature by direct quenching and is taken up.
The processing of described steel band is preferably deformation heat (thermomechanical), therefore after direct quenching, does not carry out tempering.Although observed the tempering not needing to increase cost on product, with the product made from steel that described method manufactures, there is good mechanical property.Tempering does not significantly improve the mechanical property of product, and it makes described complicate.
The preferred embodiment of the present invention discloses in claims 2 and 3.
The major advantage of method of the present invention is that it allows to have good mechanical property, comprises the product made from steel of bendability and predetermined composition in the simple and mode of economy and uses simple device fabrication.
The invention further relates to the product manufactured in method steps of the present invention.
Strip 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 inevitable impurity, and the microstructure that it is characterized in that described steel is Low Carbon Iron ferritic and/or low-carbon bainite substantially, and comprises high-carbon island; The yield strength of described steel is 650-800MPa, and post-rift elongation is at least 12%; The yield tensile ratio of described steel is 0.8-0.95; And when the yield strength of described steel in described rolling direction and the yield strength on the direction transverse to described rolling direction at the most 6.5% different, the structure of described steel is isotropic.Preferably, described steel maintains the bending radius of 0.4≤R≤0.75t and does not have macroscopic crack or crackle, and t is the thickness of described product made from steel.Preferably, the average grain size of described strip product is 2 to 4 microns.Preferably, the carbon equivalent of described strip product is at the most 0.45.Preferably, the yield strength of described strip product is more than 680MPa.Preferably, the shock strength of described strip product is at least 200J/cm at the temperature of-20 DEG C
2and/or be at least 190J/cm at the temperature of-40 DEG C
2and/or be at least 180J/cm at the temperature of-60 DEG C
2.Preferably, described strip product can be cut at the cutting gap place of the 10-15% of sheet gauge and not have visually perceptible crackle.Preferably, the steel of described strip product forms the Ti+Nb+V > 0.15 that also meets the demands.Preferably, the thickness of described strip product is 2-6mm, and the content of described steel interalloy element nb, Ti and V is: Nb:0.04-0.06, Ti:0.06-0.10, V:0.06-0.10.Preferably, the molybdenum content of described strip product is Mo < 0.10.Preferably, the molybdenum content of described steel is Mo < 0.05.Preferably, the thickness of described strip product is more than 8mm, and the copper and mickel content of described steel is 0.3≤Cu≤0.5 and Ni < 0.1%.
Obtain high strength, but the microstructure of described steel is primarily of Low Carbon Iron ferritic and/or bainite composition, and does not comprise being rich in the martensite of carbon or being rich in the bainite of carbon of significant quantity.As recommended, principal phase is by the ferrite almost with ferritic microstructure completely, and as recommended, and in the minimum island of enrichment carbon content, the austenite of a small amount of bainite and/or martensite and/or remnants forms.Remarkable reason for the high strength obtained is in the steel produced by present method, use niobium and titanium as microalloy element.Niobium and titanium must be used.
The preferred embodiment of the present invention is disclosed in appended claim 5-15.
The major advantage of product made from steel of the present invention is relative to its composition, its good mechanical property, comprises bendability and shear property and impact value.Described steel is also applicable in cold conditions (arctic condition) completely.Steel of the present invention due to its performance relevant to Engineering Task be very useful because its bendability is good, and the very effective optimization that its isotropic strength property allows it to use.In addition, little bending radius is convenient to the work of bent products planner especially.Strip product of the present invention is especially suitable for use as strong structure iron.
Accompanying drawing explanation
Also will disclose the present invention with reference to accompanying drawing in more detail below, wherein:
Fig. 1 shows method steps of the present invention;
Fig. 2 is the schematic diagram that in crooked test, V-is bending;
Fig. 3 shows the example of successful bend test results;
Fig. 4 shows the example of the bend test results of failure;
Fig. 5 represents the transition curve of the but shellfish-V (charpy-V) obtained by steel of the present invention and reference steel;
Fig. 6 shows yield strength isotropy and associating between strip-rolling; And
Fig. 7 shows yield strength isotropy and associating between coiling temperature.
Embodiment
Fig. 1 shows for the production of having the method steps of the present invention that 2 arrive the strip product of 12mm wall thickness.Described manufacture is 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 inevitable impurity.
Described steel has the low carbon content C of 0.04 to 0.08%, and it considers that the shock strength of described material, bendability and weldability are favourable.
Silicon, Si, can be used as reductor (killing agent) (in addition to aluminum) and strengthen (toughener) for ferrite with the amount of 0 to 0.50%.If object is surface quality good especially, then silicone content must be constrained to lower than 0.25%.
Manganese, the alloy content of Mn is 1.0 to 2.2%.Because low carbon content, so steel is not inclined to manganese and carbon segregation during casting, it also improves microstructural homogeneity at the high level place of Mn.Preferably, at least 1.3% manganese by alloying with realize high strength and guarantee at the most 2.0% weldability.
Steel of the present invention can be cut into the part (steel part, sheet) of precise measure by heat (such as, by laser and plasma body) and machinery.Observe, obtain the part with more level and smooth cutting surfaces.This has favorable influence for fatigue strength.In addition, during low carbon content prevents thermal cutting, cutting surfaces becomes coarse, and reduces highest hardness, and cutting surfaces is comparatively not easy to become fragile and crack between the Formation period 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, cleaved products (result) remain level and smooth and without fracture, therefore, the grinding separated of cutting surfaces or thermal cutting optional, it significantly decreases machining tolerance (performance tolerance, allowances), and decrease the quantity of manufacturing step, which thereby enhance manufacturing processed.
In order to realize good shock strength and bendability, as the phosphorus that impurity exists, the amount (at the most 0.03%) of P and sulphur, the amount (at the most 0.015%) of S is limited.The maximum of P is preferably 0.015%, and the maximum of S is preferably 0.005%.In addition, where necessary, by Ca or the CaSi process with fusing, can improving SNR.As reductor, employ aluminium Al 0.01-0.15%.The amount of the aluminium used is preferably at the most 0.05%.
The nitrogen used, the amount of N be at the most 0.01%, because when existing in the steel at titaniferous, the hard titanium nitride particles of the bendability of nitrogen formation weakening steel.The preferred amounts of nitrogen used is at the most 0.006%.
Copper, the content of Cu is reduced at the most 0.3%, to guarantee the good surface quality of hot-rolled strip.If copper content is more than 0.3%, also alloying (fusion) is recommended at least to equal the nickel of the amount of 0.25 times of Cu content, Ni.Although steel also achieves its good performance when not having copper, it can be used as necessary, to gain in strength a little.Cu content is at the most 0.5%.Especially arrive the thicker strip of 12mm for such as 8, preferably use the copper of alloy 0.3-0.5% and the nickel of at least 0.1%.
Even if do not have copper in described alloy, Ni is also restricted at the most 0.5%.Although steel also achieves its good strength property when not mixing Ni, if desired, it can be gained in strength a little.
Boron, B completely not by alloying (fusion) because it unnecessarily will increase sclerosis.Therefore the Boron contents in strip product of the present invention is restricted to impurity level, i.e. B < 0.0005%.
Titanium, T, can by alloying (fusion) to realize the strength level expected.Typically be 0.06-0.16%, although higher Ti level also can be used, its intensity increasing action is minimum in said case, and the casting of workpiece can be made complicated.Lower Ti per-cent is not used, because like this, does not use more expensive alloying or increases carbon content to being just difficult to more than 0.08% obtain high strength.It is shocking, even if the present invention shows at low temperature, as at-40 DEG C and-60 DEG C, titanium also reduces the shock strength of basic agent indistinctively, shown by the measuring result by table 3.
Chromium, Cr, and molybdenum, Mo, does not need by alloying (fusion).They are the elements increasing sclerosis and at least when higher amount, weldability is had to disadvantageous effect.For this reason, Cr is restricted to the maximum level of 0.2%, and similarly, Mo is restricted to the maximum level of 0.2%.The amount of chromium is preferably less than 0.1%.
Molybdenum be preferably allowed to at the most 0.10% amount, most preferably at the most 0.5% amount because the mechanical property of steel of the present invention is provided the titanium of the alloying element cost more can afforded than molybdenum and is realized by override by alloying (fusion).Molybdenum may be even harmful for intensity in the strip product of direct quenching of the present invention.In any situation, when product is produced by thermomechanical treatment, the molybdenum added also improves the intensity of strip product of the present invention indistinctively.
Vanadium, V, does not need by alloying (fusion).In addition, which increase unnecessary sclerosis, and for weldability, there is disadvantageous effect at least in higher concentrations.For this reason, V is restricted to the maximum level of 0.1%.
But, especially to the low tape thickness t with 2 to 6mm, when high rolling load, in order to reduce rolling load, Nb and Ti concentration is limited as follows: Nb:0.04-0.06% and Ti:0.06-0.10%, the vanadium concentration V of 0.06-0.10% can be selected to obtain high strength simultaneously.
For low tape thickness t=2-6mm, silicon also can advantageously be added into the amount of Si:0.30-0.50%, to gain in strength, as shown in the table 1 of test that carries out with Experimental composition (composition) E1.
According to the preferred embodiment of the present invention, the summation of niobium, titanium and vanadium concentration is greater than 0.15%, that is, Ti+Nb+V > 0.15%, and strip product is used as structure iron strong especially.
Especially when lower carbon content limits, strip product of the present invention is fabulous in bending (backfin) and welding, e.g., is welded in pipe or pipe fine strain of millet by automatic high frequency (HF).Manufacture experiment and shown that described material is very suitable for producing the pipe fine strain of millet of HF-welding.
The workpiece of steel is that 210mm is thick, such as, and is heated to the austenitizing temperature of 1280 DEG C, is kept about 3 hours herein.Certainly, the thickness of steel workpiece can be different from the thickness disclosed here, and austenitizing temperature can differently be selected, but recommends the scope of 1200-1350 DEG C.If austenitizing temperature is lower than the lower limit provided, then there is such risk: micro alloying element can not dissolve in austenite, that is, the austenite of homogeneous can not be obtained.Most preferably, annealing time changes in the scope of 2-4 hour.
Carbon equivalent C+Mn/6+ (the Cr+Mo+V)/5+Ni+Cu of steel)/15 preferably not higher than 0.45, which ensure that the good welds of steel.
After austenitizing, steel workpiece at the temperature of 950-1250 DEG C by hot rolling to the thickness being generally 25-50mm, be typically immediately transferred to strip mill subsequently to be rolled into the band of the final thickness with 2-12mm.The final thickness of the recommendation of steel band is at least 4mm.Final thickness is also recommended to be no more than 10mm.
In strip mill, the quantity of passage is generally 5 to 7.Final pass in strip mill is implemented at the temperature range place of 760-960 DEG C, is recommended as 780-850 DEG C.
In the end after passage, the direct quenching of steel band started in 15 seconds.In the beginning of direct quenching, the temperature of steel band is necessary at least 700 DEG C.Direct quenching is implemented with the quench rates of 30-150 DEG C/sec as water quenching, and the upper limit of recommendation is 120 DEG C/sec at the most.Direct quenching continues until the temperature of 300 DEG C at the most, and the temperature of recommendation is 100 DEG C.After direct quenching, steel is taken up immediately.Therefore, coiling temperature can fall in the temperature range of 30-300 DEG C.The initial coiling temperature recommended is 100 DEG C at the most, because when steel is taken up at the temperature more than 100 DEG C, the discontinuous steam cushion of described complicate can be formed on the steel surface.
As the result of thermomechanical treatment, the microstructure of steel becomes even, and forms mutually by dominating, and it is preferably Low Carbon Iron ferritic and/or low-carbon bainite.The amount of leading phase is usually more than 90%.In other words, the upper bainite of very low amounts and/or residual austenite and/or martensite exist in high carbon group.Average grain size (granularity) in microstructure is less, is preferably about 2-4 micron.Also necessarily first described microstructure does not comprise large crystal grain, and therefore, consider the intensity of steel, described steel has curved characteristic good especially.Grain-size must be homogeneous as far as possible and meticulous, and it is realized by method of the present invention.
Table 1 below provides the example of the concentration of steel of the present invention and the example of Fabrication parameter and the intensity utilizing them to obtain and toughness value to 3.In order to compare, table 2 and 3 also comprises the Fabrication parameter of the scope not belonging to method of the present invention, that is, do not correspond to the process of method of the present invention.In table 2, for Fabrication parameter, and in table, mechanical strength properties is illustrated with R with reference to test.
The curved characteristic that other the theming as detected utilizes process of the present invention to obtain, these are compared with the curved characteristic obtained by the Fabrication parameter outside scope of the present invention, see table 3 and 4, steel B3Q23 (according to crooked test of the present invention a)) and steel A3M33 (the crooked test b outside the present invention)).
Index T_f in table 2 represents temperature during last rolling pass, and index T_c represents temperature when batching beginning, and index Th represents the thickness of steel band, and index Wi represents the width of steel band.
In the first row of table 3, T represents such sample, and its intensity and toughness are determined on the direction of crossing take-up direction.End (ending) L represents such sample, and its intensity and toughness are determined in take-up direction.
Composition (subject composition) tested by table 1.
| 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 | 0.006 | 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 | 0.058 | 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 | 2a | 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 | Bending b |
| B3Q23 | 830 | 50 | 10 | 1270 | 9 | Bending 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 | Bending c |
table 3. intensity and toughness properties
Table 2 and 3 shows when direct quenching is implemented into low temperature (50 DEG C), and impact value is good, and intensity is isotropically high.
As from table 3 see, be 635-829MPa according to the yield strength of steel of the present invention.Post-rift elongation A5 is at least 12%, is generally at least 15%.The yield tensile ratio (yield strength/breaking tenacity) of steel is about 0.8-0.95.
Can reach a conclusion further 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 in the machine direction of steel band and cross-machine direction each other and inapparent difference.Yield strength on machine direction is almost equally high with the yield strength in cross-machine direction, and the ratio of intensity is < 6.5%, even < 2%.According to embodiment, Strength Changes low be like this by implement according to the preferred embodiment of the present invention to be quenched into lower than 100 DEG C temperature and/or by utilizing the final band rolling temperature of 890 DEG C to obtain.
As shown in table 2 and 3, described homogeneous quality is present in wherein final rolling temperature lower (lower than 890 DEG C) and/or batch at low temperature in the steel of (coiling temperature 50 DEG C).
Reference value from table shows, for embodiment 1,2a and 5, when coiling temperature is more than 100 DEG C, the isotropy of hardness of steel value is reduced to the value close to 10%, this representative for routine, the usual change of intensity level of steel that deformation heat is produced.This is equally applicable to breaking strength values.
The isotropic effect of final flexure temperature T_f and coiling temperature T_c to yield strength is checked in figs. 6 and 7 in more detail, and it shows that the reduction of final flexure temperature and coiling temperature allows the yield strength of steel of the present invention to be enhanced.
The present invention also shows that yield strength isotropy can utilize formula Rp (T-L)/Rp (L)=-46.6+0.0576T_f+0.0103T_c to assess, and wherein T_f is final flexure temperature, and T_c is coiling temperature.
Homogeneous quality is favourable, because when the steel band being used for different object is designed, does not need to consider such fact, that is, described steel band in take-up direction than on the direction of crossing take-up direction, there is higher intensity.Therefore, when all, that is, also when cutting is processed to the blank of product (it in use accepts their maximum load on the direction of take-up direction corresponding to steel band), the high strength of steel band can be utilized.In addition, the use of steel band can be optimised, because do not need to be considered about the Strength Changes of loading direction.In addition, isotropic intensive property may contribute to the bending formation of the homogeneous quality not considering bending direction (longitudinal/horizontal), this further improves the suitability of strip product of the present invention.Table 4 shows that the bendability (it is known is problematic) in longitudinal bending is fabulous.Such as, steel sample B5Q3, allows the R/t value reaching 1.3 in longitudinal bending.The transverse bend of this steel still successfully reaches the R/t value of 0.3.
Bend and implemented as the V-between the instrument of upper and lower is bending by art methods, Fig. 3 shows principle.Bending method used is the free bend of the V-A/F V with 100mm.Test block is bent in the two directions, and they are curved Z-shaped thus.
Table 4. bends result.Bend with the square plate of the side length with 300-400mm, and 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 successfully bending (good) with circular bending shape and full surface.Underproof result (failure) is that in the region due to bending radius, visible crackle, slight crack or corner angle cause.Table 5 shows the typical bending mistake causing defective result, and table 4 shows the example of bending (failure) of obviously failure.
The typical bending defect of table 5. (failure, lost efficacy, faults)
As shown in Figure 4, (crooked test in table 2 a) has the bendability more much better than steel A3M33 (the crooked test b in table 2) to steel B3Q23.In steel of the present invention, the ratio (R/t) of bending radius and the strength of materials can be even 0.4, and is only about 1.6 by the ratio that the conventional reference steel manufactured reaches.The conclusion drawn from table 1 to 4 and Fig. 5 is in the method for the invention, and direct quenching is proceeded to the temperature of 300 DEG C at the most.
As shown in table 3 and Fig. 5, the impact value obtained from steel sample B4Q23 (transition curve d) is significantly good than the impact value obtained from steel sample A2M33 (transition curve c).Steel sample is above by the temperature (with reference to table 2) of direct quenching to 50 DEG C, and the latter is cooled to the temperature of 615 DEG C.The typical impact value of steel that table 3 also shows to be cooled to the high temperature of about 600 DEG C (embodiment 1 and 10) only to cause for this intensity rank.As shown, at the temperature of-20 DEG C, the shock strength of steel of the present invention is at least 200J/cm
2, and/or be at least 190J/cm at the temperature of-40 DEG C
2, and/or be at least 180J/cm at the temperature of-60 DEG C
2.
Finally, the present invention illustrates by the information described in more detail in testing example and table 1 to 4.
embodiment 1.strip mill is used to the hot steel band that rolling has the thickness of 5mm and the composition (A1) of table 1.Rolling parameter (A1M33) illustrates in table 2.Result (A1M33) illustrates in table 3.Result shows, when steel band is taken up under the coiling temperature of 600 DEG C, realize fabulous intensity, but shock strength is still only at normal level.Noticeable aspect is that yield strength is obviously different on different measurement directions, and its micro-alloyed steel for the hot pair rolling of deformation is normal.Elongation level is normal.
embodiment 2.strip mill is used to the hot steel band that rolling has the thickness of 5mm and the composition (A1) of table 1.Rolling parameter (A1M63) illustrates in table 2.Result illustrates in table 3.But result shows, batches and produce low strength the steel (A1M63) of the impact energy improved under lower coiling temperature (about 480 DEG C).Elongation level is normal.Described band is cooled to the intensity (close to normal level) that still lower cooling temperature (about 250 DEG C) improves steel (A1Q61), wherein significantly improves impact energy.Elongation is still lower than normal level.
embodiment 3.strip mill is used to the hot steel band that rolling has the thickness of 5mm and the composition (A1) of table 1.Rolling parameter (A1M83) illustrates in table 2.Result (A1M83) illustrates in table 3.Result shows, intensity is brought up to close to normal good level by batching under low-down coiling temperature (about 50 DEG C), and wherein impact energy is still significantly better than normal level.Elongation is still lower than normal level.
embodiment 4.strip mill is used to the hot steel band that rolling has the thickness of 8mm and the composition (B4) of table 1.Rolling parameter (B4Q23) illustrates in table 2, and corresponding result illustrates in table 3.Result shows, intensity is brought up to normal level by batching under low-down coiling temperature (about 50 DEG C), and provides significantly better than normal impact energy.Further, it should be noted that yield strength in rolling direction is almost identical horizontal and vertical.Elongation is slightly lower than normally.
embodiment 5.strip mill is used to the hot steel band that rolling has the thickness of 10mm and the composition (B2) of table 1.Rolling parameter (B2L13) illustrates in table 2, and corresponding result illustrates in table 3.Result shows, under very high rolling temperature (910 DEG C), and batching under the coiling temperature of 360 DEG C, the longitudinal yield strength on bending direction is still in low-level, but impact energy is still good.Elongation is roughly in normal level.
embodiment 6.strip mill is used to the hot steel band that rolling has the thickness of 10mm and the composition (B3) of table 1.Rolling parameter (B3Q25) illustrates in table 2, and corresponding result illustrates in table 3.Result shows, under low-down rolling temperature (about 800 DEG C) and under low-down coiling temperature (about 50 DEG C), for thicker strip, yield strength also brings up to normal level, and wherein shock strength is still in good level.Noticeable aspect is identical horizontal and vertical about the yield strength of rolling direction.Elongation is slightly lower than normal level.
embodiment 7.strip mill is used to the hot steel band that rolling has the thickness of 5mm and the composition (D1) of table 1.Rolling parameter (D1Q63) illustrates in table 2, and corresponding result illustrates in table 3.Result shows, when steel is quickly cooled to the temperature of 50 DEG C, the minimizing of alloying element (especially Ti, Nb) greatly reduces intensity.Elongation and shock strength are in good level.
embodiment 8.strip mill is used to the hot steel band that rolling has the thickness of 7.7mm and the composition (C1) of table 1, and described steel band is used to square (quadratic) pipe fine strain of millet that manufacture has the HF-welding of the size of 100mm × 250mm subsequently.Rolling parameter (C1Q35) illustrates in table 2, and illustrates in table 3 from the result that pipe fine strain of millet is measured.The intensity level measured is the intensity that pipe fine strain of millet forms rear acquisition.Because there is cold shaping in the manufacture of pipe fine strain of millet, therefore impact value declines usually slightly.Result shows also to be very suitable for manufacturing double-strength pipe fine strain of millet according to the steel of described method.
embodiment 9.strip mill is used to the hot steel band that rolling has the thickness of 8mm and the composition (A3 and B4) of table 1.Rolling parameter (A3M33 and B3Q23) illustrates in table 2, and illustrates in table 3 from the corresponding test result that described steel band is measured.Table 4 shows the bending comparison of these steel (A3M33 and B3Q23), notices that the steel B3Q23 of direct quenching remains bending good at R/t value 0.4 place thus.The steel A3M33 of the temperature of about 600 DEG C is cooled to can successfully to be bent to R/t value 1.6.
embodiment 10.fig. 5 compares the impact value at different probe temperature place steel A2M33 and B4Q23 by but shellfish V shock test.Composition and the Fabrication parameter of steel A2M33 and B4Q23 illustrate in tables 1 and 2.The steel B4Q33 of direct quenching proves obviously better, also maintains its intensity at very low temperature.
embodiment 11.strip mill is used to the hot steel band that rolling has 5 and the thickness of 6mm and the composition (E1) of table 1.Rolling parameter (E1Q11 and E1Q33) illustrates in table 2, and illustrates in table 3 from the corresponding test result that described steel band is measured.Result shows, strip product of the present invention also can manufacture in little thickness, such as, by selecting the niobium of following steel, titanium and content of vanadium: 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 that rolling has the thickness of 12mm and the composition (F1 and F2) of table 1.Rolling parameter (F1Q23 and F2Q43) illustrates in table 2, and illustrates in table 3 from the corresponding test result that described steel band is measured.Result shows, strip product of the present invention also can manufacture with thick size.In addition, this embodiment proves further by being implemented into lower than the direct quenching of the temperature of 100 DEG C and/or by utilizing the strip-rolling outlet temperature lower than 890 DEG C to obtain homogeneous quality.
Hereinbefore, the present invention is described by embodiment.Due to this, it should be noted, details of the present invention can be implemented in every way within the scope of the appended claims.
Claims (14)
1., by utilizing steel to manufacture a method for the hot rolled strip product with 2 to 12mm thickness, the composition of described 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 inevitable impurity, it is characterized in that:
-under the austenitizing temperature of 1200 to 1350 DEG C the workpiece of austenitizing steel;
-in pre-rolling step steel workpiece described in hot rolling;
-in strip mill the steel workpiece of pre-rolling described in rolling, make the rolling temperature in the end passage, described workpiece being reached to 760 to 960 DEG C; And
-in described strip mill after described final pass, the rate of cooling with 30 to 150 DEG C/sec is cooled by one step, by described steel band direct quenching to 300 DEG C at the most, make the average grain size in the microstructure of described steel be 2 to 4 microns, described direct quenching is carrying out in 15 seconds from described final pass.
2. method according to claim 1, is characterized in that, the outlet temperature of described direct quenching is 100 DEG C at the most.
3. method according to claim 1 and 2, is characterized in that, described steel band is shaped as pipe product after described direct quenching.
4. a hot rolled strip product, has thickness and the following composition by weight percentage of 2-12mm:
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 inevitable impurity, it is characterized in that, the average grain size in the microstructure of described steel is 2 to 4 microns and the microstructure of described steel comprises high-carbon island for Low Carbon Iron ferritic substantially and/or low-carbon bainite,
The yield strength of described steel is 650-800MPa, and post-rift elongation is at least 12%; The yield tensile ratio of described steel is 0.8-0.95; And
When the yield strength of described steel in described rolling direction and the yield strength on the direction transverse to described rolling direction at the most 6.5% different, the structure of described steel is isotropic.
5. strip product according to claim 4, is characterized in that, in transverse bend, described steel maintains the bending radius of 0.4t≤R≤0.75t, and do not have macroscopic crackle or crack, wherein t is the wall thickness of described product made from steel.
6. strip product according to claim 4, is characterized in that, the carbon equivalent of described strip product is at the most 0.45.
7. strip product according to claim 4, is characterized in that, the yield strength of described strip product is more than 680MPa.
8. the strip product according to any one of aforementioned claim 4 to 7, is characterized in that, the shock strength of described strip product is at least 200J/cm at the temperature of-20 DEG C
2and/or be at least 190J/cm at the temperature of-40 DEG C
2and/or be at least 180J/cm at the temperature of-60 DEG C
2.
9. strip product according to claim 4, is characterized in that, described strip product can be cut at the cutting gap place of the 10-15% of sheet gauge and not have visually perceptible crackle.
10. strip product according to claim 4, is characterized in that, described steel forms the Ti+Nb+V>0.15 that also meets the demands.
11. strip product according to claim 10, is characterized in that, the thickness of described strip product is 2-6mm, and the content of described steel interalloy element nb, Ti and V is:
Nb：0.04-0.06
Ti：0.06-0.10
V：0.06-0.10。
12. strip product according to claim 10, is characterized in that, the molybdenum content of described steel is Mo<0.10.
13. strip product according to claim 4, is characterized in that, the molybdenum content of described steel is Mo<0.05.
14. strip product according to claim 4, is characterized in that, the thickness of described strip product is more than 8mm, and the copper and mickel content of described steel is 0.3≤Cu≤0.5 and Ni<0.1%.
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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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| CN102439179B true CN102439179B (en) | 2015-03-25 |
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| EP (1) | EP2430199B1 (en) |
| CN (1) | CN102439179B (en) |
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| FI122313B (en) * | 2010-06-07 | 2011-11-30 | Rautaruukki Oyj | Process for the production of hot rolled steel product and hot rolled steel |
| WO2013007729A1 (en) | 2011-07-10 | 2013-01-17 | Tata Steel Ijmuiden Bv | Hot-rolled high-strength steel strip with improved haz-softening resistance and method of producing said steel |
| FI20125379L (en) * | 2012-04-03 | 2013-10-04 | Rautaruukki Oyj | Method for making high strength malleable continuous annealed steel strip and high strength malleable continuously annealed steel strip |
| FI124825B (en) * | 2013-02-22 | 2015-02-13 | Rautaruukki Oyj | Process for producing a metal-coated and hot-worked steel component and metal-coated steel strip product |
| EP3097214B1 (en) * | 2014-01-24 | 2021-02-24 | Rautaruukki Oyj | Hot-rolled ultrahigh strength steel strip product |
| SI2924140T1 (en) * | 2014-03-25 | 2018-04-30 | Thyssenkrupp Steel Europe Ag | Method for manufacturing a high strength flat steel product |
| CN104526115B (en) * | 2014-11-04 | 2017-01-18 | 南方增材科技有限公司 | Electric smelting forming method for nuclear power station pressure vessel shell |
| WO2016198906A1 (en) | 2015-06-10 | 2016-12-15 | Arcelormittal | High-strength steel and method for producing same |
| CN109414904B (en) | 2016-05-10 | 2022-10-28 | 美国钢铁公司 | High strength steel product and annealing process for manufacturing the same |
| US11560606B2 (en) * | 2016-05-10 | 2023-01-24 | United States Steel Corporation | Methods of producing continuously cast hot rolled high strength steel sheet products |
| CN107236909B (en) * | 2017-06-16 | 2019-06-18 | 武汉钢铁有限公司 | It can be used for the high intensity, high tenacity corrosion resistant steel and its production method of -60 DEG C of low temperature environments |
| CN108300949B (en) * | 2018-02-12 | 2020-01-17 | 天津理工大学 | Method for orientationally distributing bundled bainite in steel |
| CN109100378B (en) * | 2018-07-24 | 2021-01-01 | 华北理工大学 | Method for analyzing residual austenite in low-carbon bainite steel |
| EP3653736B1 (en) * | 2018-11-14 | 2020-12-30 | SSAB Technology AB | Hot-rolled steel strip and manufacturing method |
| CN109487163B (en) * | 2018-12-13 | 2020-08-28 | 河钢股份有限公司 | Direct quenching type 800 MPa-level yield structural steel plate and production method thereof |
| CN111349759B (en) * | 2020-03-30 | 2021-09-28 | 武汉钢铁有限公司 | Production method of thin-specification wear-resistant steel for DQ (data-on-demand) process |
| CN113172980B (en) * | 2021-05-12 | 2023-01-03 | 北京科技大学 | Preparation method of stainless steel/carbon steel composite sheet strip |
| CN114150215B (en) * | 2021-10-19 | 2022-10-21 | 首钢集团有限公司 | Low-alloy high-strength steel for automobiles and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1195708A (en) * | 1996-12-31 | 1998-10-14 | 阿斯克迈塔尔公司 | Steel and process for manufacture of steel component formed by cold plastic deformation |
| EP1375694A1 (en) * | 2002-06-19 | 2004-01-02 | Rautaruukki OYJ | Hot-rolled steel strip and method for manufacturing the same |
Family Cites Families (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5531842A (en) * | 1994-12-06 | 1996-07-02 | Exxon Research And Engineering Company | Method of preparing a high strength dual phase steel plate with superior toughness and weldability (LAW219) |
| JP3425837B2 (en) * | 1996-03-28 | 2003-07-14 | 株式会社神戸製鋼所 | High-strength hot-rolled steel sheet, high-strength galvanized steel sheet excellent in pitting corrosion resistance and crushing properties, and methods for producing them |
| ATE346960T1 (en) * | 1997-07-28 | 2006-12-15 | Exxonmobil Upstream Res Co | MANUFACTURING PROCESS FOR ULTRA-HIGH-STRENGTH, WELDABLE STEELS WITH EXCELLENT TOUGHNESS |
| FR2807068B1 (en) * | 2000-03-29 | 2002-10-11 | Usinor | HOT ROLLED STEEL WITH VERY HIGH LIMIT OF ELASTICITY AND MECHANICAL STRENGTH FOR USE IN PARTICULAR FOR THE PRODUCTION OF PARTS OF MOTOR VEHICLES |
| DE10062919A1 (en) * | 2000-12-16 | 2002-06-27 | Thyssenkrupp Stahl Ag | Process for producing hot strip or sheet from a microalloyed steel |
| DE10161465C1 (en) | 2001-12-13 | 2003-02-13 | Thyssenkrupp Stahl Ag | Production of hot strip used in vehicle chassis comprises casting steel into pre-material, hot rolling to form hot strip, cooling in first cooling step, and cooling in second cooling step after pause to coiling temperature |
| JP4214006B2 (en) * | 2003-06-19 | 2009-01-28 | 新日本製鐵株式会社 | High strength steel sheet with excellent formability and method for producing the same |
| JP2006299415A (en) * | 2005-03-24 | 2006-11-02 | Jfe Steel Kk | Method for producing hot-rolled steel sheet for low yield-ratio electric-resistance welded steel tube excellent in low temperature toughness |
| RU2292404C1 (en) * | 2005-07-15 | 2007-01-27 | Открытое акционерное общество "Северсталь" | Strip making method for producing tubes |
-
2009
- 2009-05-11 FI FI20095528A patent/FI20095528A/en not_active Application Discontinuation
-
2010
- 2010-04-16 WO PCT/FI2010/050310 patent/WO2010130871A1/en active Application Filing
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1195708A (en) * | 1996-12-31 | 1998-10-14 | 阿斯克迈塔尔公司 | Steel and process for manufacture of steel component formed by cold plastic deformation |
| EP1375694A1 (en) * | 2002-06-19 | 2004-01-02 | Rautaruukki OYJ | Hot-rolled steel strip and method for manufacturing the same |
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| RU2011149763A (en) | 2013-06-20 |
| EP2430199B1 (en) | 2019-05-29 |
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| FI20095528A0 (en) | 2009-05-11 |
| WO2010130871A1 (en) | 2010-11-18 |
| ES2738876T3 (en) | 2020-01-27 |
| EP2430199A1 (en) | 2012-03-21 |
| RU2535890C2 (en) | 2014-12-20 |
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| PL2430199T3 (en) | 2019-12-31 |
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