CN101003878A - Low yield ratio fire-resistant steel - Google Patents
Low yield ratio fire-resistant steel Download PDFInfo
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- CN101003878A CN101003878A CNA2006101274697A CN200610127469A CN101003878A CN 101003878 A CN101003878 A CN 101003878A CN A2006101274697 A CNA2006101274697 A CN A2006101274697A CN 200610127469 A CN200610127469 A CN 200610127469A CN 101003878 A CN101003878 A CN 101003878A
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- C—CHEMISTRY; METALLURGY
- C09—DYES; PAINTS; POLISHES; NATURAL RESINS; ADHESIVES; COMPOSITIONS NOT OTHERWISE PROVIDED FOR; APPLICATIONS OF MATERIALS NOT OTHERWISE PROVIDED FOR
- C09K—MATERIALS FOR MISCELLANEOUS APPLICATIONS, NOT PROVIDED FOR ELSEWHERE
- C09K21/00—Fireproofing materials
- C09K21/02—Inorganic materials
- C09K21/04—Inorganic materials containing phosphorus
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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
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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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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10S57/00—Textiles: spinning, twisting, and twining
- Y10S57/904—Flame retardant
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Abstract
Provided is a refractory steel which has high strength of 50-60 kg level (the tensile strength at room temperature is 490-590 MPa) and exhibits low yield ratio and fire resistance at the same time. Said refractory steel, base on the mass %, contains C: 0.04-0.15%; si: 0.1-1.0%; Mn: 1.0-2.0%; P: lower than 0.020%; S: lower than 0.010%; Al: 0.005-0.050%; Ti: 0.02-0.08%; Cu: 0.50-2.5%; N: 0.002-0.010%; Mo 0-0.20% except 0.20%; Nb: 0-0.005% except 0.005%; V: 0-0.005% except 0.005%; and Fe as well as unavoidable impurities, with a MS value mentioned below of 4.2-6.5%, wherein the number of Cu containing precipitate with a particle diameter of 5-30 nm within the visual field area 1 mu m2 is lower than 250. MS=5[C]+[Mn]+[Ni]+2[Cu].
Description
Technical field
The present invention relates to a kind of fire-resistant steel, it is suitable for for example might exposing to the open air the structural lumber under the high temperature of fire etc.
Background technology
General structural steel is can guarantee the mode of full intensity down in room temperature (normal temperature) and to design that still, if it is in the condition of high temperature more than 500 ℃, then intensity significantly reduces.Therefore,, to implement fire-resistant covering, so that its unlikely becoming fragile under the condition of high temperature, and occur that works collapses or significant deformation steel owing to fire etc. is exposed in the pyritous building structural steel material.
Fire-resistant covering like this because also can improve building cost, causes the long periodization of duration in addition, so in recent years, exploitation has need not implement the fire-resistant steel that intensity also can be at high temperature kept in this fire-resistant covering.For example, in the fair 4-50362 communique of spy (patent documentation 1), record the trickle carbide that utilizes Mo, Nb, V etc. and the steel of precipitation strength.But, this steel that utilize the precipitation strength element to strengthen, because difficulty is controlled in suitable the separating out of precipitate, though will pursue low yielding ratio from the aspect of shock resistance, its yield ratio but rises, and is therefore very insufficient as steel for building.
With respect to this, such as the spy open flat 8-333626 communique (patent documentation 2) record, the applicant has proposed a kind of fire-resistant steel, its under the Mo and Cr prerequisite of specified amount, the V of compound interpolation 0.010～0.050% and/or 0.005～0.030% Nb, thereby both can keep the high temperature yield point, suppress the rising of the yield strength under the normal temperature simultaneously, still, its strength level is low, intensity under the high temperature (yield-point) deterioration is also big, is inadequate as fire-resistant steel.
On the other hand, open the addition that proposes to have reduction Mo, Nb, V in the flat 2-263916 communique (patent documentation 3), and apply flexibly the low yielding ratio steel plate for building that has excellent fire-resistance of the precipitation strength of the Cu under the high temperature the spy.But this steel plate tensile strength at room temperature mainly is 40～50 feather weight, if become 60 kg class, then the reduction of yield ratio is insufficient.In addition, open in the 2002-249845 communique (patent documentation 4) the spy, record the addition that suppresses Mo, Nb, V, and applied flexibly the fire-resistant steel of the precipitation strength of Cu, still, the reduction of yield ratio still is insufficient.
[patent documentation 1] special fair 4-50362 communique
[patent documentation 2] spy opens flat 8-333626 communique
[patent documentation 3] spy opens flat 2-263916 communique
[patent documentation 4] spy opens the 2002-249845 communique
Summary of the invention
As mentioned above, having the sufficient low yielding ratio under the normal temperature and the High Strength Steel of hot strength (resistivity against fire) concurrently is not developed so far, the objective of the invention is to, a kind of fire-resistant steel is provided, it has 50～60 kg class, and (high strength of the tensile strength 490～590MPa) under the normal temperature is low yielding ratio simultaneously and have excellent resistivity against fire.
Fire-resistant steel of the present invention, in quality %, containing: C:0.04～0.15%, Si:0.1～1.0%, Mn:1.0～2.0%, P:0.020% are following, S:0.010% is following, Al:0.005～0.050%, Ti:0.02～0.08%, Cu:0.50～2.5%, N:0.002～0.010%, Mo:0～be lower than 0.20%, Nb:0～be lower than 0.005%, V:0～be lower than 0.005%, and Fe and unavoidable impurities, following MS value is 4.2～6.5%, visual field area 1 μ m
2The Cu precipitate that contains that middle particle diameter is 5nm～30nm is lower than 250.
MS＝5×[C]+[Mn]+2×[Cu]
Wherein, the quality % of [X] expression element X.
Mo, Nb, three kinds of elements of V, because separate out after hot rolling, institute is so that the yield ratio rising, but according to fire-resistant steel of the present invention, because be as having limited the predetermined component of the content of these three kinds of elements,, welded H AZ toughness having been improved so can stably realize low yielding ratio.In addition, with the positive interpolation of Ti and the interpolation of Cu, can not damage HAZ toughness, hot strength (high temperature yield point) is improved, and can access excellent resistivity against fire by also.Particularly, contain Cu precipitate amount, can guarantee the Cu of solid solution in steel, promote separating out of when high temperature Cu thus, and can access excellent hot strength by restriction.In addition,, can normal temperature strength further be improved thus with not damaging hot strength, can promote the reduction of yield ratio in view of the above by will can easily making an amount of martensite that generates in the tissue as the MS value of the index of stabilization of austenite as 4.2～6.5%.
In described fire-resistant steel, by dividing rate as 10～35% martensite, intensity is further improved, yield ratio is further reduced.In addition, can also add as intensity and improve more than one the element of selecting in A group's's (B:0.0005～0.0050%, Ni:0.1～3.0%, Cr:0.1～1.0%) the element of element; Can also add as HAZ toughness and improve more than one the element of selecting in B group's (Zr:0.005～0.050%, Ca, Mg, REM (rare earth element): be respectively 0.0005～0.0050%) the element of element.In addition, following MS ' value is 4.2～6.5%,
MS’＝5×[C]+[Mn]+[Ni]+2×[Cu]
Wherein, the quality % of [X] expression element X.
According to fire-resistant steel of the present invention because suppressed to make Mo, Nb that yield ratio rises, V interpolation and with it as predetermined component, so the yield ratio normal temperature is under reduced, can make shock resistance raising and HAZ tenacity excellent.In addition,, thereby promote the solid solution of Cu, the Cu of solid solution is separated out, so can guarantee excellent hot strength because also limit the number that contains the Cu precipitate by Ti, the Cu that adds specified amount.In addition, this manufacture method is also easy, and productivity is good.
Embodiment
The chemical ingredients of fire-resistant steel of the present invention at first, is described.Below, unit is quality %.
C：0.04～0.15％
C adds as strengthening element.It if surpass 0.15%, then can't form ferrite on the other hand in the intensity that is difficult to below 0.04% to guarantee more than the 490MPa, forms cold tissue, and yield ratio rises.Therefore, the following of C amount is limited to 0.04%, is preferably 0.05%, is limited to 0.15% on it, is preferably 0.12%.
Si：0.1～1.0％
Its interpolation of Si is in order to ensure intensity and deoxidation.This effect is low excessively when being lower than 0.1%, if surpass 1.0%, then hard MA tissue (martensite and austenitic mixed structure) increases, HAZ toughness deterioration on the other hand.Therefore, the following of Si is limited to 0.1%, is preferably 0.12%, is limited to 1.0% on it on the other hand, is preferably 0.80%.
Mn：1.0～2.0％
Mn is used to guarantee intensity and adds.When being lower than 1.0%, can not get prescribed strength, if surpass 2.0%, then can't form ferrite on the other hand, formed the cold yield ratio of organizing and rise.Therefore, the following of Mn is limited to 1.0%, is preferably 1.2%, is limited to 2.0% on it, is preferably 1.8%.
Below the P:0.020%
P is the impurity element that encourages intercrystalline failure.In order to ensure ductility, reduce yield ratio and be suppressed at below 0.020%, preferably be suppressed at below 0.012%.
Below the S:0.010%
S is the fissured impurity element of high temperature that encourages HAZ, and the viewpoint from HAZ toughness is guaranteed is suppressed at it below 0.010%, preferably is suppressed at 0.008%.
Al：0.005～0.050％
Al adds as deoxidant element.Be lower than at 0.005% o'clock because deoxidation is insufficient, so ductility reduce, on the other hand if be higher than 0.050% the same with Si, make the increase of hard MA tissue, HAZ toughness deterioration.Therefore, the following of Al amount is limited to 0.005%, is preferably 0.010%, is limited to 0.050% on it, is preferably 0.040%.
Ti：0.020～0.08％
Separate out owing to Ti becomes carbide, thereby hot strength is improved.On the other hand, if it surpasses 0.08%, then separating out significantly of carbide risen yield ratio.Therefore, the following of Ti amount is limited to 0.02%, is preferably 0.025%, is limited to 0.08% on it, is preferably 0.070%.
Cu：0.50～2.5％
Cu improves hot strength by the precipitation strength of Cu, helps the formation of martensitic stucture simultaneously as austenite stabilizer element.But, if its excessive interpolation then causes hot workability reduction, weldability (HAZ toughness) to reduce.Therefore, the following of Cu amount is limited to 0.50%, is preferably 0.70%, is limited to 2.5% on it, is preferably 2.0%.
N：0.002～0.010％
N combines with the part of Ti and forms TiN, helps the HAZ flexible to improve.This effect is low excessively when it is lower than 0.002%, on the other hand if it surpasses 0.010%, the amount of separating out of TiC is reduced, and institute is so that hot strength also reduces, and nitride becomes HAZ toughness is reduced in addition.Therefore, the following of N amount is limited to 0.0020%, is preferably 0.0025%, is limited to 0.010% on it on the other hand, is preferably 0.008%.
Mo:0～0.20% but do not comprise 0.20%
Mo in addition, makes thickization of bainite structure of HAZ because yield ratio is reduced, and toughness is reduced, thus few more be preferred more.Can not add yet.In composition of the present invention, allow it to be lower than 0.20%, preferably be suppressed at below 0.16%.
Nb, V: be respectively 0～0.005% but do not comprise 0.005%
Same with Mo, because the reduction of yield ratio, make HAZ toughness deterioration and few more more for preferred.Can not add yet.In composition of the present invention, allow it to be lower than 0.005%, preferably be suppressed at below 0.004%.
MS value (=5 * [C]+[Mn]+[Ni]+2 * [Cu]): 4.2～6.5%
C, Mn, Ni, Cu are effective elements on intensity improves, by being to add these elements more than 4.2% with the MS value, can easily obtain the high-strength steel of 60 kg class, but these elements are austenite stabilizer element, excessive interpolation is austenitizing when high temperature easily, and hot strength is reduced.Therefore, the upper limit of MS value is suppressed at 6.5%.
Fire-resistant steel of the present invention, except that described basal component, surplus is made of Fe and unavoidable impurities, but improve element as intensity (normal temperature) in addition, can also add more than one the element of selecting in the element from A group (B, Ni, Cr), improve element as HAZ toughness, can also add more than one the element of selecting in the element from B group (Zr, Ca, Mg, REM (rare earth element)), and form the composition of following (1), (2), (3).
(1) basal component+from A group's more than one element
(2) basal component+from B group's more than one element
(3) composition of described (1)+from B group's more than one element
Illustrate that described characteristic improves the addition of element, and more specifically effect.
B：0.0005～0.0050％
B helps intensity to improve, but because excessive interpolation intensity is excessive, institute is so that the reduction of HAZ toughness.Therefore, its addition can be more than 0.0005%, but below 0.0050%.
Ni：0.1～3.0％
Ni can not make HAZ toughness deterioration, and intensity is improved, but excessive because of excessive interpolation intensity, institute is so that the reduction of HAZ toughness.Therefore, its addition can be more than 0.1%, but below 3.0%.
Cr：0.1～1.0％
Cr is also the same with Ni, can not make HAZ toughness deterioration, and intensity is improved, but it also is saturated excessively adding its effect, causes material cost to increase.Therefore, its addition can be for more than 0.1%, but below 1.0%.
Zr：0.005～0.050％
Because utilizing the formation of nitride, Zr improves HAZ toughness, so preferred interpolation more than 0.005%.On the other hand, excessively add if it is higher than 0.050%, then thickization of nitride makes HAZ toughness reduce on the contrary.Therefore, preferably be suppressed at below 0.050%.
Ca, Mg, REM: be respectively 0.0005～0.0050%
The form balling that these elements have by making inclusion improves the flexible effect.Preferably add more than 0.0005% for this reason.On the other hand, excessively add, then form oxide compound, HAZ toughness is reduced if it is higher than 0.0050% respectively.
Fire-resistant steel of the present invention has described chemical ingredients, and still, in order further to guarantee solid solution Cu amount, particle diameter is that the number that contains the Cu precipitate of 5～30nm size will be limited in visual field area 1 μ m
2In be lower than 250.If described precipitate is more than 250, then the yield ratio under the room temperature rises, and the solid solution capacity deficiency of Cu, and the Cu amount of separating out at high temperature reduces, and hot strength is reduced.
In addition, the tissue of fire-resistant steel of the present invention, manufacture method is indicated as described later, comprise martensite (M) about 2～10%, in addition, for ferrite (F), bainite (B) or comprise their complex tissue jointly, still, fire-resistant steel of the present invention also can be the tissue arbitrarily of F+M, B+M, F+B+M.But, divide rate, be preferably 10～35% about martensite, can be more preferably 20～35%.By with it as 10～35%, can obtain easily that yield ratio is low, the steel of 60 kg class.When it was lower than 10%, the reduction effect of yield ratio was little, and not on the one hand if surpass 35%, the yield ratio that makes on the contrary really up to the mark that then becomes rises.
Fire-resistant steel of the present invention, its manufacturing are the steel by the described composition of melting, this steel billet is heated to temperature about 1100～1200 ℃ after, final rolling temperature is finished hot rolling as about 850 ℃, cool off.About the speed of cooling after the hot rolling, for the number that contains the Cu precipitate that makes specified dimension is in per 1 μ m
2Be lower than 250, and 800～500 ℃ speed of cooling need be made as 5 ℃/more than the sec.When being lower than 5 ℃/sec, the number of the described Cu of containing precipitate will be separated out in a large number and be higher than 250.For make speed of cooling be in 5 ℃/more than the sec, after the hot rolling steel water-cooled is got final product, at this moment, adjust cooling water inflow according to thickness of slab, thereby can adjust speed of cooling.
In the speed of cooling below 500 ℃, in composition of the present invention, (0.5～1 ℃ of speed of cooling/sec) arrives 200 ℃ as the martensitic transformation end temp, thereby generates martensite about 2～10%, helps the raising of intensity, the reduction of yield ratio by air cooling.In addition, by 500～200 ℃ speed of cooling is made as 2.5 ℃/more than the sec, martensite branch rate is increased to more than 10%, can yield ratio further be reduced.By the water-cooled steel, can make speed of cooling become 2.5 ℃/more than the sec, speed of cooling is fast more, martensite divides rate to rise more thereupon.For martensite branch rate is become about 35%, adjust cooling water inflow according to thickness of slab, carry out 800～200 ℃ cooling with speed of cooling following about 30 ℃/sec.
Next, enumerate embodiment hot-rolled steel sheet of the present invention and manufacture method thereof are more specifically illustrated, but the present invention and can't help this embodiment and determinate explanation.
[embodiment]
Steel grade shown in the melting table 1,2 is heated to 1150 ℃ with this steel billet, implements hot rolling, final rolling end temp is finished as 850 ℃ rolling, with the cooling of the speed of cooling shown in the table 3, the test steel plate of making thickness of slab 50mm.In method of cooling, speed of cooling is that the following air cooling that utilizes of 1 ℃/sec cools off, and the above water-cooled of utilizing of 2.5 ℃/sec is cooled off.
Take the structure observation test film from thickness of slab 1/4 position of each test portion steel plate, use transmission electron microscope (TEM) to observe 5 visuals field for 200,000 times, measure the particle diameter that contains the Cu precipitate with multiplying power, and statistics visual field area 1 μ m
2In particle diameter be the number of 5～30nm.Described particle diameter adopts image software (Image-Pro of Micromedia corporate system) to measure the area that contains the Cu precipitate, and each is tried to achieve diameter of equivalent circle from its area, with it as particle diameter.In addition, similarly measure the martensitic area in the area of visual field, try to achieve martensite branch rate divided by the visual field area with it.Table 3 shows this measurement result.
In addition, use the steel plate of each test portion, carry out the normal temperature tension test.Measure yield-point (YS) and tensile strength (TS), try to achieve yield ratio (YR).In addition, carry out 600 ℃ high temperature tension test, measure YS.Tension test, is implemented according to JISZ2241 by steel plate processing tension test sheet according to JISZ2201.This measurement result of table 3 expression.Room temperature tensile strength is more than the 490MPa, and YR is more than 75%, and high temperature YS/ normal temperature YS is evaluated as qualified level more than 75%.
In addition, in order to investigate weldability the test portion steel plate is implemented thermal cycling test.Thermal cycling test, as being equivalent to the thermal cycling that welding heat input is 25kJ/cm, be to be heated to after 1400 ℃ to be cooled to 500 ℃ thermal cycling from 800 ℃ with 200sec and to apply 1 time, behind the thermal cycling test, take the shock test sheet from steel plate, implement pendulum impact test (0 ℃ of test temperature), measure impact absorbency characteristic absorption energy (vE0).VE0 is evaluated as the qualified level of HAZ flexible more than the 100J.Table 3 shows test-results.
As shown in Table 3, test portion No.1～25 of example, room temperature tensile strength is more than the 490MPa, and YR is below 75%, and high temperature YS/ normal temperature YS is more than 75% simultaneously, can guarantee suitable intensity in 600 ℃ the condition of high temperature.And the result of thermal cycling test also can guarantee 100J, has good HAZ toughness concurrently.Particularly, it comprises martensite 20～35%, and normal temperature strength is more than 600MPa, and YR is controlled at below 71%, and hot strength, HAZ toughness are also excellent in addition.
[table 1]
Annotate: the No.1-20 of examination section is an example ,-be not have to add.
[table 2]
Annotate: band * number is comparative example among the No. of examination section ,-be not have to add, it is outside the invention scope that the numerical value that rolls off the production line is arranged.
[table 3]
| Test portion NO. | Separate out control | Organizational controls | The normal temperature characteristic | Hot properties | Weldability | |||||
| 800-500 ℃ of speed of cooling ℃/sec | Cu contains precipitate number/μ m 2 | 500-200 ℃ of speed of cooling ℃/sec | M divides rate % | YS WPa | TS WPa | YR ％ | YS MPa | High temperature YS/normal temperature YS | HAZ toughness vEO J | |
| 1 | 15.0 | 65 | 0.5 | 3 | 369 | 492 | 75％ | 302 | 82％ | 223 |
| 2 | 14.5 | 100 | 1.0 | 3 | 375 | 511 | 73％ | 300 | 80％ | 212 |
| 3 | 12.5 | 90 | 0.5 | 5 | 376 | 515 | 73％ | 303 | 81％ | 163 |
| 4 | 15.0 | 100 | 1.0 | 5 | 366 | 494 | 74％ | 293 | 80％ | 245 |
| 5 | 13.5 | 80 | 0.5 | 8 | 367 | 496 | 74％ | 297 | 81％ | 238 |
| 6 | 14.5 | 85 | 1.5 | 4 | 374 | 503 | 74％ | 302 | 81％ | 175 |
| 7 | 15.5 | 80 | 0.5 | 6 | 367 | 500 | 73％ | 297 | 81％ | 257 |
| 8 | 15.0 | 75 | 0.5 | 7 | 385 | 523 | 74％ | 313 | 81％ | 162 |
| 9 | 14.0 | 50 | 1.0 | 5 | 383 | 512 | 71％ | 315 | 83％ | 158 |
| 10 | 15.5 | 110 | 0.5 | 6 | 374 | 503 | 74％ | 297 | 80％ | 174 |
| 11 | 13.5 | 100 | 1.0 | 5 | 369 | 502 | 74％ | 295 | 80％ | 165 |
| 12 | 15.0 | 90 | 0.5 | 9 | 323 | 516 | 72％ | 300 | 81％ | 178 |
| 13 | 14.5 | 100 | 1.0 | 3 | 367 | 499 | 74％ | 294 | 80％ | 126 |
| 14 | 14.0 | 90 | 1.0 | 8 | 442 | 610 | 72％ | 356 | 81％ | 174 |
| 15 | 13.5 | 110 | 0.5 | 8 | 465 | 630 | 74％ | 370 | 80％ | 155 |
| 16 | 15.0 | 90 | 1.0 | 8 | 451 | 613 | 74％ | 363 | 81％ | 168 |
| 17 | 15.5 | 90 | 0.5 | 7 | 496 | 669 | 74％ | 399 | 81％ | 121 |
| 18 | 16.0 | 90 | 1.0 | 5 | 395 | 535 | 74％ | 318 | 81％ | 110 |
| 19 | 12.5 | 100 | 0.5 | 8 | 455 | 632 | 72％ | 364 | 80％ | 177 |
| 20 | 12.0 | 120 | 1.0 | 9 | 467 | 627 | 74％ | 369 | 79％ | 204 |
| 21 | 14.5 | 80 | 2.5 | 20 | 445 | 629 | 71％ | 350 | 81％ | 159 |
| 22 | 14.5 | 85 | 5.5 | 35 | 449 | 662 | 68％ | 363 | 81％ | 175 |
| 23 | 15.5 | 75 | 2.5 | 15 | 366 | 503 | 73％ | 297 | 81％ | 169 |
| 24 | 15.0 | 60 | 5.0 | 25 | 369 | 544 | 68％ | 303 | 82％ | 203 |
| 25 | 10.0 | 90 | 0.5 | 9 | 451 | 623 | 68％ | 363 | 81％ | 164 |
| *26 | 15.0 | 95 | 5.0 | 20 | 344 | 488 | 70％ | 276 | 80％ | 131 |
| *27 | 15.0 | 50 | 5.5 | 45 | 476 | 629 | 76％ | 393 | 83％ | 94 |
| *28 | 14.5 | 90 | 5.0 | 35 | 362 | 540 | 67％ | 291 | 81％ | 85 |
| *29 | 15.0 | 80 | 6.0 | 35 | 320 | 485 | 65％ | 268 | 84％ | 125 |
| *30 | 13.5 | 100 | 5.5 | 45 | 531 | 692 | 77％ | 425 | 80％ | 115 |
| *31 | 12.5 | 55 | 6.0 | 40 | 482 | 701 | 68％ | 396 | 82％ | 45 |
| *32 | 15.0 | 75 | 5.0 | 30 | 442 | 620 | 71％ | 331 | 75％ | 144 |
| *33 | 16.0 | 50 | 5.5 | 35 | 463 | 596 | 78％ | 382 | 83％ | 72 |
| *34 | 15.0 | 25 | 4.5 | 25 | 428 | 614 | 70％ | 308 | 72％ | 222 |
| *35 | 14.5 | 200 | 5.0 | 35 | 395 | 575 | 69％ | 293 | 74％ | 88 |
| *36 | 15.0 | 35 | 5.5 | 35 | 455 | 667 | 68％ | 379 | 83％ | 92 |
| *37 | 15.0 | 60 | 5.0 | 20 | 468 | 622 | 75％ | 373 | 80％ | 45 |
| *38 | 12.5 | 75 | 5.5 | 30 | 460 | 595 | 77％ | 374 | 81％ | 95 |
| *39 | 15.0 | 60 | 5.0 | 35 | 536 | 767 | 70％ | 440 | 82％ | 65 |
| *40 | 15.0 | 100 | 5.0 | 40 | 450 | 648 | 69％ | 360 | 80％ | 55 |
| *41 | 15.0 | 25 | 5.0 | 35 | 494 | 696 | 71％ | 367 | 74％ | 65 |
| *42 | 5.5 | 260 | 5.0 | 30 | 424 | 623 | 70％ | 305 | 72％ | 164 |
Annotate: band * number is comparative example among the test portion No..
Claims (6)
1. a low yield ratio fire-resistant steel is characterized in that, in quality %, contains:
C:0.04～0.15%, Si:0.1～1.0%, Mn:1.0～2.0%, P:0.020% are following, S:0.010% is following, Al:0.005～0.050%, Ti:0.02～0.08%, Cu:0.50～2.5%, N:0.002～0.010%, Mo:0～0.20% but do not comprise 0.20%, Nb:0～0.005% but do not comprise 0.005%, V:0～0.005% but do not comprise 0.005% and Fe and unavoidable impurities, following MS value is 4.2～6.5%, visual field area 1 μ m
2The Cu precipitate that contains that middle particle diameter is 5nm～30nm is lower than 250,
MS＝5×[C]+[Mn]+2×[Cu]
Wherein, the quality % of [X] expression element X.
2. fire-resistant steel according to claim 1 is characterized in that, in described steel tissue, martensite branch rate is 10～35%.
3. fire-resistant steel according to claim 1 and 2 is characterized in that, also contains in B:0.0005～0.0050%, Ni:0.1～3.0%, Cr:0.1～1.0% more than one in quality %.
4. fire-resistant steel according to claim 3 is characterized in that, following MS ' value is 4.2～6.5%,
MS＝5×[C]+[Mn]+[Ni]+2×[Cu]
Wherein, the quality % of [X] expression element X.
5. fire-resistant steel according to claim 1 and 2 is characterized in that, also contains in Zr:0.005～0.050%, Ca:0.0005～0.0050%, Mg:0.0005～0.0050%, REM:0.0005～0.0050% more than one in quality %.
6. fire-resistant steel according to claim 3 is characterized in that, also contains in Zr:0.005～0.050%, Ca:0.0005～0.0050%, Mg:0.0005～0.0050%, REM:0.0005～0.0050% more than one in quality %.
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| Application Number | Priority Date | Filing Date | Title |
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| JP2006010025A JP4656417B2 (en) | 2006-01-18 | 2006-01-18 | Low yield ratio refractory steel |
| JP2006010025 | 2006-01-18 |
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| CN101003878A true CN101003878A (en) | 2007-07-25 |
| CN100453679C CN100453679C (en) | 2009-01-21 |
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| Country | Link |
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| JP (1) | JP4656417B2 (en) |
| KR (1) | KR100799822B1 (en) |
| CN (1) | CN100453679C (en) |
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| CN102560256A (en) * | 2012-02-29 | 2012-07-11 | 江苏省沙钢钢铁研究院有限公司 | Fire-resistant weather-resistant steel with excellent low-temperature toughness and preparation process thereof |
| CN104561819A (en) * | 2014-11-26 | 2015-04-29 | 南京钢铁股份有限公司 | Q460-grade fire-resistant weathering steel and preparation method thereof |
| CN105624578A (en) * | 2016-01-20 | 2016-06-01 | 广西丛欣实业有限公司 | Fire resistant steel for building |
| CN111996453A (en) * | 2020-08-13 | 2020-11-27 | 北京科技大学 | Multi-precipitation enhanced type anti-seismic, corrosion-resistant and fire-resistant H-shaped steel and preparation method thereof |
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| KR101018131B1 (en) * | 2007-11-22 | 2011-02-25 | 주식회사 포스코 | High strength and low yield ratio steel for structure having excellent low temperature toughness |
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| JPH0757886B2 (en) * | 1988-07-14 | 1995-06-21 | 新日本製鐵株式会社 | Process for producing Cu-added steel with excellent weld heat-affected zone toughness |
| JPH06104856B2 (en) * | 1989-04-03 | 1994-12-21 | 新日本製鐵株式会社 | Manufacturing method of low yield ratio steel plate with excellent fire resistance for construction |
| JPH04362156A (en) * | 1991-06-05 | 1992-12-15 | Sumitomo Metal Ind Ltd | Steel excellent in fire resistance and toughness in welded joint part |
| JP3296591B2 (en) | 1992-05-27 | 2002-07-02 | 川崎製鉄株式会社 | Low yield ratio high strength hot rolled steel sheet and method for producing the same |
| JP3831146B2 (en) * | 1999-05-06 | 2006-10-11 | 新日本製鐵株式会社 | Manufacturing method of hot-rolled steel sheet for processing with excellent fatigue characteristics |
| JP2001123224A (en) * | 1999-10-27 | 2001-05-08 | Sumitomo Metal Ind Ltd | Method for producing high strength and high toughness non-heattreated parts |
| JP3528759B2 (en) * | 2000-06-12 | 2004-05-24 | 住友金属工業株式会社 | Cu-aged steel and method for producing the same |
| JP4362219B2 (en) * | 2000-10-11 | 2009-11-11 | 新日本製鐵株式会社 | Steel excellent in high temperature strength and method for producing the same |
| JP3718637B2 (en) * | 2001-02-22 | 2005-11-24 | 株式会社神戸製鋼所 | Refractory steel with excellent weldability |
| CN1132958C (en) * | 2001-10-17 | 2003-12-31 | 武汉钢铁(集团)公司 | High-performance refractory weather-resisting building steel and its production method |
| US7513959B2 (en) * | 2002-12-05 | 2009-04-07 | Jfe Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102560256A (en) * | 2012-02-29 | 2012-07-11 | 江苏省沙钢钢铁研究院有限公司 | Fire-resistant weather-resistant steel with excellent low-temperature toughness and preparation process thereof |
| CN102560256B (en) * | 2012-02-29 | 2013-12-25 | 江苏省沙钢钢铁研究院有限公司 | Fire-resistant weather-resistant steel with excellent low-temperature toughness and preparation process thereof |
| CN104561819A (en) * | 2014-11-26 | 2015-04-29 | 南京钢铁股份有限公司 | Q460-grade fire-resistant weathering steel and preparation method thereof |
| CN104561819B (en) * | 2014-11-26 | 2017-05-24 | 南京钢铁股份有限公司 | Q460-grade fire-resistant weathering steel and preparation method thereof |
| CN105624578A (en) * | 2016-01-20 | 2016-06-01 | 广西丛欣实业有限公司 | Fire resistant steel for building |
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Also Published As
| Publication number | Publication date |
|---|---|
| JP2007191747A (en) | 2007-08-02 |
| CN100453679C (en) | 2009-01-21 |
| KR100799822B1 (en) | 2008-01-31 |
| JP4656417B2 (en) | 2011-03-23 |
| KR20070076529A (en) | 2007-07-24 |
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