CN101171354A - Heat-resistant steel product and method for production thereof - Google Patents
Heat-resistant steel product and method for production thereof Download PDFInfo
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- CN101171354A CN101171354A CNA2006800151857A CN200680015185A CN101171354A CN 101171354 A CN101171354 A CN 101171354A CN A2006800151857 A CNA2006800151857 A CN A2006800151857A CN 200680015185 A CN200680015185 A CN 200680015185A CN 101171354 A CN101171354 A CN 101171354A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 107
- 239000010959 steel Substances 0.000 title claims abstract description 107
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 17
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 238000005096 rolling process Methods 0.000 claims description 25
- 238000001816 cooling Methods 0.000 claims description 17
- 238000000034 method Methods 0.000 claims description 15
- 229910052796 boron Inorganic materials 0.000 claims description 9
- 229910052758 niobium Inorganic materials 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052749 magnesium Inorganic materials 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract description 5
- 229910052759 nickel Inorganic materials 0.000 abstract description 2
- 239000000047 product Substances 0.000 description 17
- 239000006104 solid solution Substances 0.000 description 14
- 238000012360 testing method Methods 0.000 description 11
- 229910001563 bainite Inorganic materials 0.000 description 10
- 229910052799 carbon Inorganic materials 0.000 description 10
- 230000009970 fire resistant effect Effects 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 10
- 239000011777 magnesium Substances 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 229910052751 metal Inorganic materials 0.000 description 8
- 239000002184 metal Substances 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- 230000009466 transformation Effects 0.000 description 8
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- 230000002950 deficient Effects 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
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- 229910052750 molybdenum Inorganic materials 0.000 description 3
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- 230000033228 biological regulation Effects 0.000 description 2
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- 229920006395 saturated elastomer Polymers 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- OHVLMTFVQDZYHP-UHFFFAOYSA-N 1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-2-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]ethanone Chemical compound N1N=NC=2CN(CCC=21)C(CN1CCN(CC1)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)=O OHVLMTFVQDZYHP-UHFFFAOYSA-N 0.000 description 1
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 description 1
- LDXJRKWFNNFDSA-UHFFFAOYSA-N 2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]ethanone Chemical compound C1CN(CC2=NNN=C21)CC(=O)N3CCN(CC3)C4=CN=C(N=C4)NCC5=CC(=CC=C5)OC(F)(F)F LDXJRKWFNNFDSA-UHFFFAOYSA-N 0.000 description 1
- YLZOPXRUQYQQID-UHFFFAOYSA-N 3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]propan-1-one Chemical compound N1N=NC=2CN(CCC=21)CCC(=O)N1CCN(CC1)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F YLZOPXRUQYQQID-UHFFFAOYSA-N 0.000 description 1
- 229910052582 BN Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 229910039444 MoC Inorganic materials 0.000 description 1
- 229910018505 Ni—Mg Inorganic materials 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 208000034189 Sclerosis Diseases 0.000 description 1
- 229910007981 Si-Mg Inorganic materials 0.000 description 1
- 229910008316 Si—Mg Inorganic materials 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 150000001639 boron compounds Chemical class 0.000 description 1
- ZDVYABSQRRRIOJ-UHFFFAOYSA-N boron;iron Chemical compound [Fe]#B ZDVYABSQRRRIOJ-UHFFFAOYSA-N 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
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- 239000004615 ingredient Substances 0.000 description 1
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- 239000007788 liquid Substances 0.000 description 1
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 1
- 239000000395 magnesium oxide Substances 0.000 description 1
- AXZKOIWUVFPNLO-UHFFFAOYSA-N magnesium;oxygen(2-) Chemical compound [O-2].[Mg+2] AXZKOIWUVFPNLO-UHFFFAOYSA-N 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
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- 238000007254 oxidation reaction Methods 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012797 qualification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000002784 sclerotic effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000013517 stratification Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Classifications
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
-
- 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
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Rolling (AREA)
Abstract
Provided are a heat-resistant steel product excellent in the heat resistance, which is reduced in the variation in the material quality and can exhibit, even at 600 DEG C, a yield strength of not less than 2/3 times that at an ordinary temperature; and a method for producing the heat-resistant steel product. A heat-resistant steel product characterized in that it comprises 0.01 to 0.03 mass % of C, 0.2 to 1.7 mass % of Mn, 0.5 mass % or less of Si, 0.7 to 2 mass % of Cu, 0.8 mass % or less of Mo, 0.01 to 0.3 mass % of Nb, 0.005 to 0.03 mass % of Ti, 0.006 mass % or less of N, 0.0003 to 0.003 mass % of B, 0.2 mass % or less of V, 1 mass % or less of Cr, 0.1 mass % or less of Al, 0.03 mass % or less of P, 0.02 mass % or less of S, Ni in an amount satisfying a mass ratio of Ni/Cu of 0.6 to 9.0 and the balance of Fe and inevitable impurities, and exhibits a yield strength at 600 DEG C of 60 % or higher of that at 21 DEG C.
Description
Technical field
The present invention relates to the used heat-resistant steel product and the manufacture method thereof such as structure unit of buildings.
Background technology
From the aspect such as advanced of the superelevation stratification of buildings, architectural design technology, economizing overall planning according to Japan's construction has carried out restudying of fire-resistant design, and clear and formulated " new fire-resistant design method " in March, 62.According to this regulation, removed of the restriction of the temperature of steel when making fire in the old law order that requires fire-resistant coating below 350 ℃, suitable its fire-resistant method for coating is determined on the hot strength that can be by taking into account heat-resistant steel product and the actual load ground of buildings.That is, under the situation of the design hot strength in the time can guaranteeing 600 ℃, can cut down fire-resistant coating correspondingly.
Corresponding to this trend, the applicant before opened in the flat 2-77523 communique the spy, had proposed the low yielding ratio steel for building and steel and the manufacture method thereof that have excellent fire-resistance.This aim of formerly inventing is, improves hot strength by adding Mo, Nb so that the yield-point 600 ℃ the time when reaching normal temperature more than 70%.The design hot strength of steel is set in 600 ℃ to be based on from rise and its required fire-resistant coating construction cost aspect of taking into account the steel expense that alloying element brings and to consider what most economical understanding was carried out.The H shaped steel of this exploitation is characterised in that, Nb, B and Cu by low carbonization and interpolation trace, generation low-carbon bainite tissue, the yield strength in the time of 600 ℃ reach the above high-temp and high-strengthization of 293MPa, be fire-resistant 590MPa level specification normal temperature yield strength 440MPa 2/3.(yield strength is meant yield-point when yield-point is clear and definite, be meant 0.2% yield strength when yield-point is indeterminate.)
In addition, except same purpose,, open the spy and to disclose in the flat 9-137218 communique by adding the building structure H shaped steel that Mo, Cu, Ni have reduced the material fluctuation also for local fragility such as the fillet parts that improves H shaped steel.
In addition, open the spy that the fluctuation that discloses material in the flat 10-072620 communique is little, the manufacture method of the H shaped steel of welding property excellent.
Summary of the invention
The inventor etc. have tested will be by above-mentioned steel in the manufacturing of first to file technology as various shaped steel, especially because of complex-shaped starting material at the H shaped steel that is restricted aspect the rolling appearance of strictness.The result, find from difference in the final rolling temperature at web, the edge of a wing, each position of fillet, draft, speed of cooling, position according to steel, organize especially the bainite ratio obviously different, normal temperature and hot strength, ductility, toughness fluctuation, generation can not be satisfied the position of Rolled Steel For Welded Structure standards such as (JIS G3106).In addition, according to the steel of above-mentioned patent documentation 2 and patent documentation 3 manufacturings, the heat cracking that causes because of Cu produces surface imperfection, or the fire performance deterioration.
The present invention In view of the foregoing finishes, even its purpose is to provide the heat-resistant steel product that has excellent fire-resistance and the manufacture method thereof of the yield strength more than 60% that a kind of fluctuation of material is littler also can demonstrate at normal temperature the time in the time of 600 ℃.
For this reason, the inventor etc. study, found that, and the especially interpolation of Cu, the yield strength when improving 600 ℃ is effectively, because the Cu of solid solution at normal temperatures separates out in the steel tissue when high temperature.But then as can be known, if the heat cracking that produces in order to suppress to follow Cu to add and the Ni that adds is too much, then the Cu difficulty is separated out when high temperature, can not fully reach to utilize Cu to separate out the purpose that improves yield strength.Then, further carried out deep investigation, found that, by contain 0.7～2.0% Cu in quality %, and contain Ni so that the mass ratio of Ni/Cu is 0.6～0.9, promptly can balance enjoy well and suppress to follow Cu to add the heat cracking that is taken place and utilize Cu to separate out the raising yield strength.
The invention provides a kind of heat-resistant steel product, it is characterized in that: % contains in quality: C:0.01～0.03%, Mn:0.2～1.7%, below the Si:0.5%, Cu:0.7～2%, below the Mo:0.8%, Nb:0.01～0.3%, Ti:0.005～0.03%, below the N:0.006%, B:0.0003～0.003%, below the V:0.2%, below the Cr:1%, below the Al:0.1%, below the P:0.03%, below the S:0.02%, and contain Ni/Cu by quality ratio and be 0.6～0.9 Ni, surplus is made of Fe and inevitable impurity, and the yield strength in the time of 600 ℃ is more than 60% of yield strength in the time of 21 ℃.In addition, yield strength is meant yield-point when yield-point is clear and definite, is meant 0.2% yield strength when yield-point is indeterminate.
This heat-resistant steel product also can also contain any in Ca:0.0005～0.005%, Mg:0.0005～0.01%, REM:0.0005～0.01% or more than 2 kinds, surplus is made of Fe and inevitable impurity in quality %.In addition, this heat-resistant steel product for example is a shaped steel.
In addition, the invention provides a kind of manufacture method of heat-resistant steel product, it is characterized in that: beginning is rolling after strand being heated to 1200 ℃～1350 ℃ temperature province, cool off 800 ℃～500 ℃ temperature range in the rolling back of finishing with 0.1 ℃ of average out to/speed of cooling more than the s, wherein said strand contains in quality %: C:0.01～0.03%, Mn:0.2～1.7%, below the Si:0.5%, Cu:0.7～2%, below the Mo:0.8%, Nb:0.01～0.3%, Ti:0.005～0.03%, below the N:0.006%, B:0.0003～0.003%, below the V:0.2%, below the Cr:1%, below the Al:0.1%, below the P:0.03%, below the S:0.02%, and contain Ni/Cu by quality ratio and be 0.6～0.9 Ni, surplus is made of Fe and inevitable impurity.
This manufacture method also can will also contain Ca:0.0005～0.005%, Mg:0.0005～0.01%, REM:0.0005～0.01% in quality %, beginning was rolling after the strand that surplus is made of Fe and inevitable impurity was heated to 1200 ℃～1350 ℃ temperature province, cooled off 800 ℃～500 ℃ temperature range in the rolling back of finishing with 0.1 ℃ of average out to/speed of cooling s more than.In addition, the manufacture method of this heat-resistant steel product also can be for example by the rolling shaped steel of making.
According to the present invention, can access the high-intensity heat-resistant steel product that has generated the oversaturated low-carbon bainite tissue of Cu under the normal temperature.If heat-resistant steel product of the present invention is heated to 600 ℃, then separates out and to obtain hot strength by Cu.
Description of drawings
Fig. 1 is the explanatory view of reduction unit used in the embodiments of the invention.
Fig. 2 is the sectional view of the H shaped steel of taking the position of expression mechanical testing sheet.
Fig. 3 represents that schematically Ni/Cu of the present invention compares and the chart of the scope of the ratio of yield strength in the time of 600 ℃ (high temperature PS) and the yield strength (normal temperature YP) in the time of 21 ℃.
Embodiment
Below, describe the present invention in detail.
For the hot strength of steel, at roughly 1/2 below 700 ℃ of temperature of steel fusing point, the strengthening mechanism during with normal temperature is roughly the same, is waited by 1～4 following aspect and controls: 1. the miniaturization of ferrite crystal grain particle diameter; 2. the sosoloid that is produced by alloying element is strengthened; 3. dispersion-strengthened by what harden and produce mutually; 4. the precipitation strength that produces by fine precipitate.In general, the rising of hot strength can realize by the softening resistance when adding that Mo, Cr improve precipitation strength and improving high temperature by the disappearance that suppresses dislocation.But surpassing 0.03% low-carbon bainite composition in carbon content is in the steel, generates the island martensite body, and low-temperature flexibility significantly reduces, and generation can not be satisfied the position of standard.
Therefore, in the present invention, is that steel is sought to produce high tenacityization by the generation that suppresses the island martensite body by forming carbon content at the utmost point low-carbon bainite composition below 0.03%, in addition, effect by the hardening capacity of utilizing compound interpolation Nb and B to produce improves makes it that bainitic transformation stably take place, and makes Cu be solid-solubilized among the α to greatest extent at normal temperatures, in the time of 600 ℃, bring into play the precipitation strength effect of Cu to greatest extent, realized normal temperature strength, hot strength and the high tenacity of target.
Herein, in soft steel, owing to can not expect the precipitation strength that molybdenum carbide and vanadium carbide produced that fire-resistant steel in the past uses, so adopted the Cu that separates out element as metal.
Below, each composition range among the present invention and the qualification reason of rolling condition are described.In addition, each composition range is represented with quality %.
C:C is for strengthening the element that steel adds, if be lower than 0.01%, then can not get as the required intensity of structural steel.In addition, surpass 0.03% surplus and add and can between lath of bainite, generate the island martensite body, base metal tenacity is significantly descended, thus will be defined as 0.01% down, on be defined as 0.03%.
Mn:Mn is that intensity, the toughness of guaranteeing mother metal needs to add more than 0.2%, but presses the permissible scopes such as toughness, crackle of weld part, will on be defined as 1.7%.
Si:Si is to the intensity of guaranteeing mother metal, with necessary elements such as liquid steel pre-deoxidizings, if but surpass 0.5%, can in the tissue of welding heat affected zone, generate the high-carbon island martensite body of sclerotic tissue, reduce the toughness of welding joint part, so the upper limit of Si content is limited to below 0.5%.In addition, Si also can not necessarily contain.
Mo:Mo is an effective element of guaranteeing strength of parent and hot strength, if but surpass 0.8%, because hardening capacity too raises, therefore the toughness deterioration of mother metal and welding heat affected zone is limited in it below 0.8%.In addition, Mo also can not necessarily contain.
Cu:Cu is used to reduce transformation temperature, increases normal temperature strength.In addition, that does not separate out in bainitic transformation is in oversaturated Cu solid solution at normal temperatures in tissue, as 600 ℃ of heating of the use temperature of fire-resistant steel the time, on the dislocation that imports by bainitic transformation, separate out the Cu phase, by this precipitation-hardening the yield strength of mother metal is increased.But Cu separating out in this α is being lower than at 0.7% o'clock, in the Cu solid solution limit in α, do not produce and separates out, and therefore can not get described reinforcement.In addition, if surpass 2%, owing to except its precipitation strength is saturated, also reduce toughness, so Cu is limited in 0.7～2%.
Nb:Nb fixes C, N by forming the Nb carbonitride, and the boron carbonitride that promotes ferritic nucleus growth, the formation of boron compound are suppressed, the state of B that remained solid solution.In addition, because solid solution Nb slows down ferritic grain growing by drag effect, even therefore under slow speed of cooling, also the γ of phase transformation does not remain to the bainitic transformation point, helps stably to produce bainite.Therefore, being set is more than 0.01%.In addition, solid solution Nb at high temperature becomes the obstacle of dislocation moving by drag effect, also helps to guarantee hot strength.Therefore, for improving hot strength, preferably add more than 0.05%.But, if surpass 0.3%, because its effect is saturated, so consider it is limited in below 0.3% from the economy aspect.
N:N helps ferritic generation, so N content is limited in below 0.006% owing to generate boron nitride.
Al:Al is deoxidation of molten steel and the element that adds as the form fix N of AlN, if surpass 0.1%, owing to generate aluminum oxide, causes decrease of fatigue strength, is below 0.1% so be set.In addition, Al also can not necessarily contain.
Ti:Ti is for suppressing separating out of BN by minimizing and the γ grain refined of separating out the solid solution N that TiN produces, increase solid solution B amount, and the hardening capacity that improves B improves effect and the element that adds.Can improve normal temperature and hot strength thus.Therefore, be lower than at 0.005% o'clock, TiN separates out quantity not sufficient, can not bring into play above-mentioned effect, thereby the lower value of Ti amount is set at 0.005%.But if surpass 0.03%, then Guo Sheng Ti separates out TiC, because of this precipitation-hardening makes the toughness deterioration of mother metal and welding heat affected zone, so it is limited to below 0.03%.
B:B adds by trace just can improve hardening capacity, helps to improve intensity.But, in its effect deficiency that is lower than at 0.0003% o'clock, and if surpass 0.003%, then generate the iron boron compound, reduce hardening capacity.Therefore, B content is limited to 0.0003～0.003%.
Ni:Ni follows the heat cracking defective of adding Cu and producing in order to prevent when rolling, need contain by Ni/Cu than the Ni that counts more than 0.6.On the other hand, Ni reduces the Cu amount of separating out because the solid solution limit of Cu is risen, so in order to ensure hot strength, regulation contains by Ni/Cu than the Ni that counts below 0.9.
Cr:Cr is by improving hardening capacity, and is effective to the reinforcement of mother metal.But, owing to consider that from toughness and indurative aspect the surplus above 1% is added harmful, so the upper limit is defined as 1%.In addition, Cr also can not necessarily contain.
V:V adds by trace can make the rolling structure miniaturization, and strengthens by separating out vanadium carbonitride, thereby can low alloying, can improve welding characteristic.But, because the interpolation of the surplus of V causes the sclerosis of weld part or the high yield strengthization of mother metal, so the upper limit of V content is defined as 0.2%.In addition, V also can not necessarily contain.
Mg:Mg preferably adds the fine dispersion of inclusion for the formation of miniaturization by oxide compound and sulfide.Mg amount is limited to 0.0005～0.01% because: Mg is powerful deoxidant element, the magnesium oxide that crystallizes out easily in molten steel come-up separate, be not utilized so surpass 0.01% interpolation, therefore its upper limit is defined as 0.01%.The magnesium alloy that uses when in addition, adding Mg for example has Si-Mg and Ni-Mg.Adopt the reason of magnesium alloy to be, because can reduce the concentration of Mg by alloying, the reaction when inhibited oxidation magnesium generates, the security in the time of can guaranteeing to add thus, and improve the utilization ratio of Mg.
Ca, REM:Ca, REM are preferably the shape of control sulfide, oxide compound and add.Ca is limited in 0.0005～0.005%, REM is limited in 0.0005～0.01%, because: if below lower value, the sulfide that is formed by these elements, the generation of oxide compound are insufficient, if more than higher limit, thickization of oxide compound, cause toughness and ductility to descend, so they are limited in above-mentioned scope.
Amount for the P that contains as unavoidable impurities, S is not particularly limited, but owing to produce welding crack and the toughness decline that causes by solidifying segregation, therefore should be as far as possible with their amount reduction, preferred P amount is below 0.03%, and S measures below 0.02%.
The strand heating that will have above-mentioned composition is so that surface temperature reaches 1200～1350 ℃ temperature province.With Heating temperature be limited to this temperature province be because: needs heating more than 1200 ℃ in order when making shaped steel, to be easy to viscous deformation, and need make the abundant solid solutions of element such as V, Nb, so the undergage of Heating temperature is decided to be 1200 ℃ by hot-work.Consider its upper limit is defined as 1350 ℃ from performance, the economy aspect of process furnace.
In addition, being to surpass under the situation of extremely thick shaped steel of 40mm, if the speed of cooling after the rolling end is slow excessively, then generate the α tissue in large quantities in tissue, Cu separates out in α when cooling, thus the minimizing of the amount of the solid solution Cu normal temperature under.In such cases, be accompanied by the generation of α tissue, the bainite ratio reduces, but precipitation strength improves yield-point more usually, can not improve tensile strength, so along with the rising of yield ratio (YR), correspondingly vibration strength reduces.In addition, if the amount of the solid solution Cu during normal temperature reduces, then can not expect when 600 ℃ of heating, to utilize the precipitation strength of Cu phase to increase yield strength.So, the yield strength in the time of 600 ℃ be lower than in the time of 21 ℃ 60%.Therefore,, solid solution Cu amount is increased as far as possible in order the time to guarantee sufficient bainite structure in cooling, thus with the average cooling rate of 800～500 ℃ temperature range be defined as 0.1 ℃/more than the s.
So the heat-resistant steel product of making of the present invention is by adopting the alloy designs of adding micro-Nb, B and a large amount of Cu of interpolation, Cu separates out hardly in bainitic transformation, be in hypersaturated state, on the other hand, when being heated 600 ℃, the Cu of solid solution separates out in the steel tissue under the normal temperature, the yield strength in the time of can improving 600 ℃.So, heat-resistant steel product of the present invention just has excellent fire performance, even the yield strength more than 60% in the time also demonstrating normal temperature for 600 ℃.
Heat-resistant steel product of the present invention can be used as steel plates such as various shaped steel, Plate Steel such as the H shaped steel, joist steel, angle steel, channel-section steel, angle of unequal legs ﹠ thickness of the structure unit that is suitable for buildings etc. etc. and concrete enforcement.For example, when making H shaped steel by above-mentioned condition as an example of heat-resistant steel product of the present invention, by having under the normal temperature by the low-carbon bainite tissue of miniaturization, can demonstrate the homogeneous mechanical characteristic at web, the edge of a wing, each position of fillet, even in H shaped steel, cannot say for sure to demonstrate,prove the position of the edge of a wing thickness of slab 1/2 of mechanical testing characteristic, wide 1/2 position most, also have enough intensity, toughness.In addition, when 600 ℃ heating,, therefore become the high-strength fireproof rolling H shaped steel of resistivity against fire and tenacity excellent owing to demonstrate the fire performance of the excellence that produces by the precipitation strength of Cu.Because this kind H shaped steel hot properties excellence, so when being used for refractory materials for building, can reach sufficient fire-resistant purpose with 20～50% of in the past coating thickness.Like this, can have excellent resistivity against fire and flexible shaped steel, can seek to reduce cost significantly by reducing construction cost, reduction of erection time by rolling the manufacturing, can realize improving building reliability, guarantee security, improve economy etc.
Embodiment
Below, by embodiment effect of the present invention is described further.
With converter melting raw material, after adding alloy, add Ti, B, be cast as the thick strand of 240～300mm by continuous casting.The cooling of strand is to control by the water yield of the secondary cooling zone of selecting the mould below and the drawing speed of strand.Table 1 shows the chemical ingredients value of each used among embodiment steel grade.Steel grade 1～17th, within the scope of the invention, steel grade 18～38th, the comparative steel beyond scope of the present invention.
Table 1 (quality %)
The strand of each steel grade shown in the table 1 is heated to 1300 ℃, in universal rolling device row shown in Figure 1, make from process furnace 1 come out be rolled material 5 (strand) successively by roughing mill 2, milling train 3, finishing mill 4, as shown in Figure 2, be rolled into the H shaped steel with H type cross-sectional shape (H458 * 417 * 30 * 50) that constitutes by the web 6 and a pair of edge of a wing 7.In addition; make rolling Heating temperature consistent with 1300 ℃ be because; as everyone knows; in general the decline of Heating temperature can make γ crystal grain grain refined; can improve mechanical characteristics; infer the heat condition thus and represent the Schwellenwert of mechanical characteristics, can judge that this value can represent the characteristic under the following Heating temperature of this temperature.
Individual separately for each H shaped steel of manufacturing like this, 7 the thickness of slab t on the edge of a wing
2Central part (1/2t
2) and the position of 1/2 wide (1/2B) of the wide length overall in the edge of a wing (B), the acquisition test sheet has been studied mechanical characteristics.In addition, research characteristic herein is because it is believed that edge of a wing 1/2B portion mechanical characteristics in H shaped steel is minimum, by learning the mechanical testing characteristic of each H shaped steel herein.
In table 2, as the mechanical testing characteristic of the H shaped steel of making from each steel grade, ratio (600 ℃ of PS/YP are than (%)), yield ratio (YR), impact value (vE0 ℃ (J)), the fragility relative reduction in area (%) of the yield strength (yield point stress YP) when yield strength (yield point stress YP (MPa)) when 0.2% yield strength when illustrating 600 ℃ respectively (600 ℃ of PS (MPa)), normal temperature (21 ℃) and tensile strength (TS (MPa)), 0.2% yield strength (600 ℃ of PS) 600 ℃ time the and normal temperature (21 ℃).In addition, criterion of acceptability as each mechanical testing characteristic, require: the tensile strength TS during normal temperature (21 ℃) is that 590MPa is above, yield strength (YP) is the above high strength of 440MPa, and, 0.2% yield strength in the time of 600 ℃ is more than 2/3 (293MPa) of 440MPa of minimum standard of the yield strength during as normal temperature (21 ℃), and the yield strength in the time of 600 ℃ is more than 60% of yield strength in the time of 21 ℃, yield ratio YR is below 80%, impact value vE0 ℃ more than 70J, the fragility relative reduction in area is below 50%.So long as this criterion of acceptability just can surpass academy of architecture's standard, can be judged as and be suitable as heat-resistant steel product.
Table 2
| 600℃PS | YP | TS | 600 ℃ of PS/YP ratios | YR | Impact value vE0 ℃ | The fragility relative reduction in area | Remarks | ||
| Steel grade | MPa | MPa | MPa | ％ | ％ | J | ％ | ||
| The |
1 | 393 | 545 | 682 | 72.1 | 79.9 | 388 | 3 | |
| 2 | 385 | 510 | 648 | 75.5 | 78.7 | 390 | 8 | ||
| 3 | 387 | 516 | 645 | 75.0 | 80.0 | 253 | 47 | ||
| 4 | 375 | 530 | 663 | 70.8 | 79.9 | 380 | 7 | ||
| 5 | 365 | 508 | 635 | 71.9 | 80.0 | 403 | 0 | ||
| 6 | 311 | 455 | 592 | 68.4 | 76.9 | 345 | 7 | ||
| 7 | 309 | 462 | 591 | 66.9 | 78.2 | 286 | 17 | ||
| 8 | 315 | 468 | 591 | 67.2 | 79.4 | 198 | 17 | ||
| 9 | 331 | 465 | 595 | 71.2 | 78.2 | 204 | 0 | ||
| 10 | 368 | 505 | 635 | 72.9 | 79.5 | 253 | 0 | ||
| 11 | 385 | 520 | 652 | 74.0 | 79.8 | 396 | 0 | ||
| 12 | 385 | 526 | 658 | 73.2 | 79.9 | 96 | 33 | ||
| 13 | 388 | 538 | 665 | 72.1 | 80.9 | 145 | 47 | ||
| 14 | 332 | 449 | 607 | 73.9 | 74.0 | 209 | 0 | ||
| 15 | 392 | 542 | 678 | 72.3 | 79.9 | 404 | 0 | ||
| 16 | 387 | 536 | 673 | 72.2 | 79.6 | 395 | 0 | ||
| 17 | 392 | 541 | 678 | 72.5 | 79.8 | 398 | 0 | ||
| Comparative steel | 18 | 211 | 398 | 488 | 53.0 | 81.6 | 115 | 33 | |
| 19 | 249 | 379 | 536 | 65.7 | 70.7 | 58 | 87 | ||
| 20 | 380 | 535 | 669 | 71.0 | 80.0 | 35 | 93 | ||
| 21 | 286 | 424 | 543 | 67.5 | 78.1 | 121 | 47 | ||
| 22 | 392 | 530 | 667 | 74.0 | 79.5 | 12 | 100 | ||
| 23 | 291 | 458 | 615 | 63.5 | 74.5 | 304 | 33 | ||
| 24 | 379 | 638 | 842 | 59.4 | 75.8 | 57 | 93 | ||
| 25 | 369 | 503 | 631 | 73.4 | 79.7 | 98 | 33 | Produce the heat cracking defective | |
| 26 | 395 | 528 | 667 | 74.8 | 79.2 | 79 | 47 | Produce the heat cracking defective | |
| 27 | 302 | 521 | 655 | 58.0 | 79.5 | 422 | 0 | ||
| 28 | 296 | 522 | 659 | 56.7 | 79.2 | 403 | 0 | ||
| 29 | 345 | 536 | 698 | 64.4 | 76.8 | 23 | 100 | ||
| 30 | 383 | 525 | 682 | 73.0 | 77.0 | 43 | 67 | ||
| 31 | 361 | 533 | 671 | 67.7 | 79.4 | 37 | 100 | ||
| 32 | 249 | 388 | 551 | 64.2 | 70.4 | 377 | 3 | ||
| 33 | 268 | 397 | 515 | 67.5 | 77.1 | 224 | 17 | ||
| 34 | 386 | 549 | 687 | 70.3 | 79.9 | 25 | 53 | ||
| 35 | 368 | 521 | 656 | 70.6 | 79.4 | 15 | 93 | ||
| 36 | 286 | 468 | 548 | 61.1 | 85.4 | 380 | 3 | ||
| 37 | 243 | 390 | 539 | 62.3 | 72.4 | 212 | 7 | ||
| 38 | 378 | 538 | 704 | 70.3 | 76.4 | 17 | 93 | ||
Each H shaped steel made from the steel grade 1～17 that is in the scope of the invention all surpasses above-mentioned criterion of acceptability.And the part of the steel grade 18～38 (comparative steel) outside the scope of the invention can not surpass above-mentioned criterion of acceptability.Especially, Ni/Cu is than the steel grade 27,28 that surpasses 0.9, and the yield strength in the time of 600 ℃ does not reach 60% of yield strength in the time of 21 ℃.In addition, Ni/Cu produces the heat cracking defective than the steel grade 25,26 that is lower than 0.6 when rolling.
The scope of the present invention (optimum range) that the ratio (being more than 60% in the present invention) of the yield strength (normal temperature YP) in the time of herein, will be according to the scope (being 0.6～0.9 in the present invention) of Ni/Cu ratio, yield strength (high temperature PS) 600 ℃ time the and 21 ℃ is determined is shown among Fig. 3.In addition, charged to scope of the invention steel grade 27,28 and steel grade 25,26 in addition among Fig. 3.
In table 3, show mechanical testing characteristic when the rolling average cooling rate that finishes the temperature range of 800～500 ℃ of backs is changed at the steel grade 2 of table 1.The average cooling rate of the rolling temperature range that finishes 800～500 ℃ of backs all surpasses above-mentioned criterion of acceptability at 0.1 ℃/ test film 1～3 more than the s.And the rolling average cooling rate that finishes the temperature range of 800～500 ℃ of backs is lower than the test film 4 of the comparative example of 0.1 ℃/s, because speed of cooling is low excessively, has generated the α tissue in the past in large quantities at bainitic transformation, so yield ratio decline, does not satisfy criterion of acceptability.
Table 3
| Speed of cooling | 600℃ PS | YP | TS | 600 ℃ of PS/YP ratios | YR | Impact value vE0 ℃ | The fragility relative reduction in area | Remarks | ||
| Test film No | Steel grade | ℃/s | MPa | MPa | MPa | ％ | | J | ％ | |
| 1 | 2 | 1 | 379 | 505 | 651 | 75.0 | 77.6 | 366 | 0 | Example |
| 2 | 2 | 0.2 | 385 | 510 | 648 | 75.5 | 78.7 | 390 | 8 | Example |
| 3 | 2 | 0.1 | 329 | 498 | 626 | 66.1 | 79.6 | 98 | 33 | Example |
| 4 | 2 | 0.05 | 301 | 486 | 591 | 61.9 | 82.2 | 79 | 47 | Comparative example |
Even each the H shaped steel in the scope of the invention is at the edge of a wing thickness of slab 1/2 of mechanical testing characteristic that cannot say for sure to demonstrate,prove rolled section steel most, wide 1/2 position, also has the shaped steel of enough normal temperature and hot strength and resistivity against fire and tenacity excellent.In addition, though verify at H shaped steel in an embodiment, but be the H shaped steel that the rolling stock of object is not limited to the foregoing description with the present invention, also can be used in steel plates such as various shaped steel such as joist steel, angle steel, channel-section steel, angle of unequal legs ﹠ thickness, Plate Steel etc. certainly.
The present invention for example can be used for used heat-resistant steel product such as structure unit of buildings etc.
Claims (6)
1. heat-resistant steel product, it is characterized in that: % contains in quality: C:0.01～0.03%, Mn:0.2～1.7%, below the Si:0.5%, Cu:0.7～2%, below the Mo:0.8%, Nb:0.01～0.3%, Ti:0.005～0.03%, below the N:0.006%, B:0.0003～0.003%, below the V:0.2%, below the Cr:1%, below the Al:0.1%, below the P:0.03%, below the S:0.02%, and contain Ni/Cu by quality ratio and be 0.6～0.9 Ni, surplus is made of Fe and inevitable impurity, and the yield strength in the time of 600 ℃ is more than 60% of yield strength in the time of 21 ℃.
2. heat-resistant steel product as claimed in claim 1, it is characterized in that: also contain any in Ca:0.0005～0.005%, Mg:0.0005～0.01%, REM:0.0005～0.01% or more than 2 kinds, surplus is made of Fe and inevitable impurity in quality %.
3. heat-resistant steel product as claimed in claim 1 or 2 is characterized in that: described steel are shaped steel.
4. the manufacture method of a heat-resistant steel product, it is characterized in that: beginning is rolling after strand being heated to 1200 ℃～1350 ℃ temperature province, 800 ℃～500 ℃ temperature range is cooled off with the above speed of cooling of 0.1 ℃/s of average out in the rolling back of finishing, wherein said strand contains in quality %: C:0.01～0.03%, Mn:0.2～1.7%, below the Si:0.5%, Cu:0.7～2%, below the Mo:0.8%, Nb:0.01～0.3%, Ti:0.005～0.03%, below the N:0.006%, B:0.0003～0.003%, below the V:0.2%, below the Cr:1%, below the Al:0.1%, below the P:0.03%, below the S:0.02%, and contain Ni/Cu by quality ratio and be 0.6～0.9 Ni, surplus is made of Fe and inevitable impurity.
5. the manufacture method of heat-resistant steel product as claimed in claim 4, it is characterized in that: beginning is rolling after strand being heated to 1200 ℃～1350 ℃ temperature province, 800 ℃～500 ℃ temperature range is cooled off with the above speed of cooling of 0.1 ℃/s of average out in the rolling back of finishing, wherein said strand also contains Ca:0.0005～0.005%, Mg:0.0005～0.01%, REM:0.0005～0.01% in quality %, and surplus is made of Fe and inevitable impurity.
6. as the manufacture method of claim 4 or 5 described heat-resistant steel products, it is characterized in that: by the rolling shaped steel of making.
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|---|---|---|---|
| JP2005134297 | 2005-05-02 | ||
| JP134297/2005 | 2005-05-02 | ||
| JP118826/2006 | 2006-04-24 | ||
| JP2006118826A JP5098210B2 (en) | 2005-05-02 | 2006-04-24 | Refractory steel and method for producing the same |
| PCT/JP2006/309347 WO2006118339A1 (en) | 2005-05-02 | 2006-04-28 | Heat-resistant steel product and method for production thereof |
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| EP (1) | EP1878810B1 (en) |
| JP (1) | JP5098210B2 (en) |
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| CN113396236A (en) * | 2019-01-31 | 2021-09-14 | 杰富意钢铁株式会社 | H-shaped steel with protrusions and manufacturing method thereof |
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| JP4072191B1 (en) * | 2006-09-04 | 2008-04-09 | 新日本製鐵株式会社 | Refractory steel material excellent in high temperature strength, toughness and reheat embrittlement resistance, and production method thereof |
| WO2008126910A1 (en) * | 2007-04-06 | 2008-10-23 | Nippon Steel Corporation | Steel material having excellent high temperature properties and excellent toughness, and method for production thereof |
| CN102251178B (en) * | 2011-06-21 | 2012-12-05 | 北京科技大学 | Preparation method for low-alloy steel keeping constant hardness under thermal disturbance |
| JP6295632B2 (en) * | 2013-12-16 | 2018-03-20 | 新日鐵住金株式会社 | High strength H-section steel with excellent toughness |
| CN104046902B (en) * | 2014-06-30 | 2016-09-28 | 莱芜钢铁集团有限公司 | A kind of low molybdenum height titanium 590MPa level Fire-resistant Steels Used in Buildings plate and manufacture method thereof |
| CN105112783A (en) * | 2015-09-15 | 2015-12-02 | 攀钢集团攀枝花钢铁研究院有限公司 | Steel for welding structure and preparation method of steel |
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| JPH06104854B2 (en) * | 1989-02-04 | 1994-12-21 | 新日本製鐵株式会社 | Manufacturing method of low yield specific hot-rolled steel sheet for building with excellent fire resistance |
| JPH07100816B2 (en) * | 1989-05-08 | 1995-11-01 | 新日本製鐵株式会社 | Manufacturing method of low yield ratio cold rolled steel sheet for building with excellent fire resistance |
| JP3039862B1 (en) * | 1998-11-10 | 2000-05-08 | 川崎製鉄株式会社 | Hot-rolled steel sheet for processing with ultra-fine grains |
| JP3985523B2 (en) * | 2000-04-24 | 2007-10-03 | Ｊｆｅスチール株式会社 | Linear shape steel excellent in fatigue characteristics of joints and method for producing the same |
| JP4819233B2 (en) * | 2000-08-30 | 2011-11-24 | 新日本製鐵株式会社 | Aluminum alloy plate with excellent formability |
| 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 |
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| CN113396236A (en) * | 2019-01-31 | 2021-09-14 | 杰富意钢铁株式会社 | H-shaped steel with protrusions and manufacturing method thereof |
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| CN101171354B (en) | 2011-04-20 |
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| US20090087335A1 (en) | 2009-04-02 |
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