EP2235226B1 - Method for selecting composition of steel and its use - Google Patents
Method for selecting composition of steel and its use Download PDFInfo
- Publication number
- EP2235226B1 EP2235226B1 EP08856442.2A EP08856442A EP2235226B1 EP 2235226 B1 EP2235226 B1 EP 2235226B1 EP 08856442 A EP08856442 A EP 08856442A EP 2235226 B1 EP2235226 B1 EP 2235226B1
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- Prior art keywords
- steel
- concentration
- composition
- mpa
- strength
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- 229910000831 Steel Inorganic materials 0.000 title claims description 212
- 239000010959 steel Substances 0.000 title claims description 212
- 239000000203 mixture Substances 0.000 title claims description 38
- 238000000034 method Methods 0.000 title claims description 14
- 239000010955 niobium Substances 0.000 claims description 66
- 229910052799 carbon Inorganic materials 0.000 claims description 38
- 239000011572 manganese Substances 0.000 claims description 37
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 34
- 229910052758 niobium Inorganic materials 0.000 claims description 32
- 239000011651 chromium Substances 0.000 claims description 30
- 229910052750 molybdenum Inorganic materials 0.000 claims description 30
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 29
- 238000001816 cooling Methods 0.000 claims description 28
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 27
- 238000005728 strengthening Methods 0.000 claims description 27
- 229910052796 boron Inorganic materials 0.000 claims description 26
- 238000005275 alloying Methods 0.000 claims description 23
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 22
- 239000011733 molybdenum Substances 0.000 claims description 22
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 20
- 239000010949 copper Substances 0.000 claims description 18
- 238000004519 manufacturing process Methods 0.000 claims description 18
- 229910052748 manganese Inorganic materials 0.000 claims description 15
- 230000009467 reduction Effects 0.000 claims description 11
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 9
- 230000001052 transient effect Effects 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 5
- 239000000956 alloy Substances 0.000 claims description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 2
- 239000010703 silicon Substances 0.000 claims description 2
- 239000000243 solution Substances 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 229910001566 austenite Inorganic materials 0.000 description 7
- 230000009970 fire resistant effect Effects 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 238000004090 dissolution Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 229910000851 Alloy steel Inorganic materials 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000011575 calcium Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000010606 normalization Methods 0.000 description 3
- 229910000746 Structural steel Inorganic materials 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- -1 niobium carbides Chemical class 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000006260 foam Substances 0.000 description 1
- 229910052602 gypsum Inorganic materials 0.000 description 1
- 239000010440 gypsum Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 230000002452 interceptive effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 102220047090 rs6152 Human genes 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000007725 thermal activation Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 210000002268 wool Anatomy 0.000 description 1
Images
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
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Definitions
- the invention relates to a method for selecting the composition of low-alloy steel, and for manufacturing a steel product, for applications exposed to high temperatures.
- the invention also relates to a low-alloy hot rolled or normalized steel for use in applications, where endurance to high temperatures and heat resistance is required, the steel having a carbon concentration of above 0.01 percent by weight.
- This steel may be called fireproof steel and it is preferably hot-rolled.
- the invention further relates to the use of the steel of the invention.
- a special feature of fireproof structural steel is that its strength at high temperatures caused by fire is higher than conventional structural steels. In conventional structural steels, the strength decreases essentially as temperature rises, because the movement of steel dislocations becomes easier due to increasing thermal activation. The strength of fireproof steel is less sensitive to temperature increases than that of conventional structural steel.
- M-C clusters cause interactive solid solution hardening that is an effective hardening mechanism in heat-resistant steels.
- M x C y precipitations may already be in the steel in supply condition or they may be formed during the heating caused by fire.
- Patent JP2004339549 discloses a fireproof steel with a tensile strength grade of 490 MPa and yield strength grade of 325 MPa.
- the publication teaches that boron and molybdenum are necessary alloying elements (Mo: 0.1- ⁇ 0.5%, B: 0.0005-0.003%).
- manganese is limited to small concentrations (Mn 0.1- ⁇ 0.9%), and during manufacturing the cooling rate after rolling is limited to values larger than 0.3 °C/s.
- the microstructure of steel should contain 20-90% bainite with the rest being ferrite. Fire properties remain good up to 750°C.
- the publication does not teach how to select fireproof steel with a yield strength of above 355, 420, 460, 500, or 690 MPa and fire properties that remain good up to 800°C.
- Published patent JP2002173733 discloses a fireproof steel that maintains good strength up to 800°C.
- the invention is based on alloying elements that increase austenite formation temperature (A c1 ) up to 800 to 900°C.
- the publication mentions for instance the following alloying elements and their concentrations: Si 0.2-1.2%, Mn ⁇ 0.5%, 0.05% ⁇ Al ⁇ 1%, Mo 0.4-1.5%, V 0.05-0.2%.
- the tensile strength grades of the steels are 400 and 490 MPa.
- the corresponding yield strength grades are 235 and 325 MPa.
- This publication also does not teach how to manufacture fireproof steel with a yield strength of above 355, 420, 460, 500, or 690 MPa.
- JP2006241552 discloses a high-strength fireproof steel with a yield strength grade of 440 MPa and tensile strength grade of 590 MPa.
- the fire-resistance properties are mainly based on high molybdenum concentrations and rather high carbon concentrations: 0.3% ⁇ Mo ⁇ 0.7%, C 0.04-0.14%. Only a small amount of niobium is used, Nb 0.01-0.05%. According to the teachings of the publication, it is not possible to manufacture fireproof steel with a molybdenum concentration below 0.3%, carbon concentration below 0.04%, or niobium concentration above 0.05%.
- US patent application 2006/0063335 A1 discloses a high-strength fire-resistant low-alloy steel. Its fire-resistant properties are based on a relatively high molybdenum concentration and on the use of boron.
- the molybdenum concentration is preferably 0.2-1.1 wt % and boron 0.0005-0.003 wt %.
- the impact strength of the steel is not especially good, because the alloying of boron weakens it.
- Molybdenum also weakens the impact strength, and is also an expensive alloying element.
- WO 2006/093282 discloses a low alloy hot-rolled fire resistant steel and a method for manufacturing the same.
- a drawback of the above patent publications is that they do not teach how to select a composition of fireproof steel and to manufacture a steel product to correspond to a desired yield strength grade in the strength range of 355 to 690 MPa and a desired fire-resistant property (by utilizing the strengthening potential of the steel that depends on the composition of the steel).
- An object of the invention is to provide a method with which the composition of steel may be selected to correspond to a desired fire-resistance and strength at high temperatures and a method for manufacturing a steel product having said composition.
- LP 95 is the strengthening potential of the steel that provides an estimate on how much the yield strength of the steel (MPa) increases at room temperature, if steel is heated to a temperature of 600°C for one hour.
- C is the carbon concentration of the steel (wt %), when the steel is in the hot-rolled condition, and C is the carbon concentration in solution in austenite, C sol , at the normalizing temperature of the steel, when the steel is normalized steel, and Nb is the niobium concentration of steel (wt %), when the steel is in the hot-rolled condition, and Nb is the niobium concentration in solution in austenite, Nb sol , at the normalizing temperature of the steel, when the steel is normalized steel.
- the correctness of the strengthening potential has been tested to be approximately 95%, i.e., the room-temperature yield point of the steel heated to a temperature of 600 °C for one hour deducted by the yield point of the steel in delivery state will at a probability of 95% increase at least by the value LP 95 .
- the value of the strengthening potential LP 95 is preferably selected to be above 50, whereby a steel has been selected having a good fire-resistance at high temperatures and a high strength reduction coefficient (the strength does not decrease much at high temperatures).
- niobium greatly increases fire-resistance which is why the niobium concentration of steel is preferably at least 0.04 wt %. Most preferably, the niobium concentration is 0.08-0.12 wt %.
- niobium precipitates into niobium carbides, which results in a smaller grain size of steel, improved ductility and strength.
- Part of the niobium also precipitates into niobium carbides during the cooling after hot-rolling.
- part of the niobium remains in the solution when the carbon concentration of steel is very low, such as in the steel of the invention; the higher concentration of niobium, the more of it remains in solution.
- the niobium in solution joins the carbon of the steel and forms strengthening precipitations and clusters. As a result of this, the steel remains strong at temperatures caused by fire.
- the carbon concentration is at least above 0.01 wt % and preferably above 0.03 wt %.
- the maximum value of the steel strengthening potential is reached at a carbon concentration of below 0.05 wt %, which is why the upper limit for carbon concentration is preferably selected to be 0.05 wt %.
- Another reason for preferably selecting 0.05% as the upper limit for carbon concentration is that the impact strength and weldability of the steel then remain good.
- the molybdenum concentration of steel does not much increase the strengthening potential of steel, and molybdenum is also an expensive alloying element, the molybdenum concentration is preferably selected to be below 0.4 wt %.
- the greatest advantages of the method of the invention are that, at a general level, it facilitates the selection of the composition of steel and manufacturing of a steel product, for the purpose of obtaining steel with good fire-resistance properties, whereby the method also makes it possible to minimize alloying element costs.
- the method also facilitates the selection of the composition for the purpose of obtaining steel classified in various strength grades S355, S420, S460, S500, and S690 (the minimum values of yield strengths 355, 420, 460, 500, and 690 MPa).
- the steel is preferably a hot-rolled plate or strip, even though other delivery forms may also apply.
- Another object of the invention is to provide for use a fire-resistant low-alloy steel with good fire-resistance without needing to use high concentrations of expensive alloying elements in it.
- the steel is also easy to manufacture and weld.
- the steel is mainly characterised in that its composition in percentage by weight is as follows: C: above 0.01 and at most 0.05 Si: at most 0.7 Mn: 1.0-2.3 Ni: at most 1.5 Cr: at most 1.5 Mo: ⁇ 0.4 Cu: at most 0.3 Nb: 0.04-0.15 B: at most 0.004 N: at most 0.01 Al: at most 0.1 V: at most 0.02 Ti: at most 0.05 Ca: at most 0.006, whereby
- the lower limit of the carbon concentration of the steel is 0.03 wt %, because carbon increases the strengthening potential significantly.
- the niobium concentration of the steel is preferably 0.08-0.12 wt %.
- the boron concentration of the steel is above 0.0005 wt %, it is advantageous for the impact strength of the steel that at the same time the manganese concentration is above 1.6 wt % and the molybdenum concentration is below 0.1 wt %.
- the molybdenum concentration of the steel is preferably below 0.4 wt %, even though the boron concentration of the steel ⁇ 0.0005 wt %.
- the reduction coefficient of the low-alloy steel of the invention at 700°C is significantly higher than the reduction coefficient presented in SFS standard EN 1993-1-2.
- the reduction coefficient achievable for the steel is above 0.3 and more preferably above 0.4 at 700°C as measured using a transient test.
- the steel according to the invention has fire resistance is good and the fire resistance is achieved with a small amount of expensive alloying elements.
- the steel can be easily and economically manufactured for yield strength grades 355, 420, 460, 500, and 690 MPa, and its composition is suitable for both thick and thin forms.
- the steel is preferably a hot-rolled plate or strip, even though other products or forms may also apply.
- the steel according to the invention is used in applications requiring high strength at temperatures above 400°C, even 600 to 800°C. Such applications include those in which the steel must be fire resistant.
- These typically include steel structures of buildings wherein the steel is preferably used in building beams and lattice structures.
- the building beams may for instance be welded double-web Q beams or single-web I beams, in which steel is used in the entire beam or only in parts significant for fire protection, such as the top or bottom flange.
- the steel of the invention works especially well for instance in situations where the intermediate floor slab system of a building is supported by a Q beam and the bottom or top flange of the beam is not protected by the slab system or concreting, whereby the flange requires especially good fire resistance. Other fire protection means are not needed when the required part of the beam is made of the steel of the invention.
- molybdenum and boron are not necessary, even though they may be utilised (Mo: 0-0.7 wt %, preferably ⁇ 0.4 wt %, B: 0-0.0040 wt %).
- Manganese is an essential alloying element to provide strength and impact strength, which is why manganese is alloyed in 1-2.3 wt % depending on the boron concentration of the steel. It has been noted that in hot-rolled steel both molybdenum and boron reduce the impact strength of the steel, whereas by increasing the manganese concentration, the impact strength of the steels according to the invention improves.
- the transition temperature of impact strength may increase as much as 50°C when boron is alloyed in steel.
- the manganese concentration is selected to be above 1.6 wt % and/or (preferably and than or) the molybdenum concentration at most 0.1 wt%.
- the proportions of bainite and ferrite in the microstructure are not restricted.
- the invention makes it possible to design steel structures with desired fire-resistance properties at manufacturing costs that are as economical as possible.
- the correctness of the formula has been tested to be approximately 95%, i.e., the room-temperature yield point of the steel heated to a temperature of 600 °C for one hour deducted by the yield point of the steel in delivery state will at a probability of 95% increase at least by the value LP 95 .
- LP 95 > 50 and in applications requiring very high fire resistance, LP 95 > 100 is selected.
- the effect of carbon on the strengthening potential is great, and this may also be observed from the attached figure that shows steel that contains not only carbon, but also 0.04 wt % of Nb, 0.14 wt % of Cr, 0.17 wt % of Mo, and 0.76 wt % of Ni.
- the carbon concentration of the steel is at least 0.01 wt %.
- the carbon concentration of the steel is above 0.03 wt % and at most 0.05 wt %, and its niobium concentration is 0.04-0.15 wt % and more preferably 0.08-0.12 wt %.
- the aim is to keep the molybdenum concentration relatively low due to the high price of molybdenum.
- the molybdenum concentration is preferably below 0.4 wt %, and if the steel contains above 0.0005 wt % of boron, the molybdenum concentration is below 0.1 wt %.
- a r3 + °C 910 - 310 ⁇ C - 80 ⁇ Mn - 20 ⁇ Cu - 15 ⁇ Cr - 55 ⁇ Ni - 80 ⁇ Mo .
- Cooling after plate-rolling may take place freely in air or as accelerated cooling with water, for instance, as long as the cooling time from 750°C to 400°C is shorter than 5000 s which corresponds to the average cooling rate that is higher than 0.07°C/s at 750 to 400°C.
- the cooling must be accelerated with water to a temperature of 450°C or below.
- composition limits of the steel according to the invention are shown in Table 1.
- Table 2 shows compositions of steel plates according to the invention within the alloying element concentrations given in Table 1. Yield point and tensile strength values were measured for these steel plates, see Table 3.
- Table 2 Chemical compositions of plates (wt %) Plate Thickness mm Type C % Si % Mn % Cu % Cr % Ni % Mo % Nb % B % BL ST 1142-1 / -2 12 miniature 0.024 0.17 1.99 0.22 0.03 0.82 0.26 0.054 0.0003 0 4.7 1143-1 / -2 12 miniature 0.043 0.18 1.99 0.23 0.03 0.81 0.26 0.054 0.0003 0 5.3 1144-1 / -2 12 miniature 0.011 0.19 1.98 0.22 0.03 0.82 0.26 0.052 0.0003 0 4.3 1145-1 / -2 12 miniature 0.040 0.18 2.08 0.21 0.03 0.13 0.11 0.103 0.0013 1 5.6 1146-1 / -2 12 miniature 0.022 0.17 2.09 0.22 0.03 1.01 0.11
- C, Si, Mn, Cr, Mo, and Cu refer to the alloying element concentrations in percent by weight.
- C is the carbon concentration of the steel (wt %), when the steel is hot-rolled steel, and C is the carbon concentration in solution in austenite, C sol , at the normalization temperature of the steel, when the steel is normalized steel.
- CR refers to the average cooling rate at 750 to 400°C.
- the above formula predicting the yield strength is used when it is necessary to select steel that corresponds to a desired yield strength grade.
- Table 3 also proves that by selecting the composition and manufacturing parameters of the steel by using the limits and formulas of the invention, it is possible to manufacture plates for yield strength grades 420, 460, 500, or 690 MPa, for instance.
- the impact strength of the steel is also adjusted to the desired level by controlling the impurities contents (S, P, O, N), calcium processing, and rolling and cooling conditions.
- Tables 2 and 3 show that the cooling rate does not much affect the strength properties of the plates at least when the cooling rates are low, so it is easy to use the presented strengthening potential formula to design compositions for fireproof steels in such a manner that it is possible to use the same composition to manufacture both thick and thin plates and strip plates.
- the examples of Table 3 show that a given strength grade may be manufactured of the same composition regardless of the cooling rate.
- Table 4 shows calculated strengthening potentials LP 50 and LP 95 and measured strength increases. It can be noted that in only two cases of thirty three the measured strengthening potential is lower than the LP 95 prediction. The highest predicted LP 95 value is 161 MPa that is achieved with the relatively high-alloy plate 1148.
- Table 5 shows the chemical composition of three comparison steels.
- Table 5 The chemical composition of three comparison materials (wt %) Plate Thickness mm CR °C/s C % Si % Mn % Al % Nb % V % Ti % Cr % Cu % Ni % Mo % N % B % 41278-024 30 0.3 0.12 0.35 1.56 0.040 0.037 0.004 0.005 0.02 0.01 0.04 0.00 0.0068 0.0002 50902-013 20 0.4 0.14 0.36 1.50 0.042 0.040 0.039 0.017 0.02 0.01 0.48 0.00 0.0099 0.0003 14630-034 20 16 0.08 0.16 1.51 0.035 0.037 0.005 0.017 0.02 0.28 0.76 0.00 0.0060 0.0003
- Plates 41278-024 and 50902-013 were cooled freely in air. Plate 14630-034 was cooled accelerated at 750-550°C.
- Table 6 shows the mechanical properties of comparison steels rolled and after heat treatment.
- the table shows that the measured strengthening potentials, R eH (AR) - R eH (1h600°C) that correspond to the LP 50 value, are typically negative.
- the comparison steels have clearly higher carbon concentrations than the steels of the invention, and on the basis of the LP 95 formula, it is expected that EP decreases when the carbon concentration increases above approximately 0.040%.
- Table 6 The mechanical properties of comparison materials rolled and after heat treatment Plate Thick CR Rolled Heat treated 600°C ReH(600°C)-ReH(AR) mm °C/s ReH MPa Rm MPa A5 % Temp °C Time min ReH MPa Rm MPa A5 % MPa 41278-024 30 0.3 455 557 30 600 60 445 553 32 -10 50902-013 20 0.4 503 642 24 600 40 501 623 24 -2 14630-034 20 16 577 685 14 600 40 572 657 21 -5
- the fire-resistance of the plates of the invention was tested in transient tests. Their mechanical properties in delivery state are shown in Table 7.
- Table 7 The mechanical properties of plates tested in transient tests Plate No. Thickness Cooling rate As rolled Heat-treated 1h600°C Charpy V as rolled crosswise, -60 °C R p0.2 R m A R p0.2 Rm A mm °C/s MPa MPa % MPa MPa % J 74705-031 20 12 569 660 22 613 670 23 310 15874-016 12 25 569 656 21 591 652 22 207 15874-033 20 11 571 644 21 589 648 23 271
- Table 8 shows the strength properties measured by transient tests at high temperatures for the steel plates of the invention and conventional structural steels.
- transient tests the strength of the material (steel) is measured in hot tensile tests, wherein a piece of steel is loaded in a test furnace at different tensile loads by increasing the temperature from 20°C to 900°C at the same time. Yield strength values at different temperatures are measured for the material (steel) on the basis of the load tests. Yield strength is the level of stress at a selected elongation value.
- the fire resistance of the plates made according to the invention has been tested in transient tests according to the standard EN 10002-5. A transient test is suitable when there is a need to define the strength properties of the material in fire conditions.
- Table 8 shows the reduction coefficients (k y,e ) of yield points of steels at high temperatures.
- k y , ⁇ f y , ⁇ at increased temperature ⁇ / f y at room temperature , wherein f y is an effective yield point at a total elongation of 2%.
- Table 8 shows that the fire properties of the steel plates of the invention are clearly better than those of conventional structural steels: at 700°C, the reduction coefficient of the effective yield point is 82 to 90% higher in the steel of the invention than in conventional steel.
- the reduction coefficient of the steels of the invention is above 0.3 and preferably above 0.4 at 700°C, which values can be seen to be true, see Table 8.
- Table 8 Strength properties measured by transient tests at high temperatures Plate of the invention Temperature Measured reduction coefficient Reduction coefficient SFS EN 1993-1-2 Ratio °C k y, ⁇ (measured) k y, ⁇ (EN 1993-1-2) k y, ⁇ (measured) / k y, ⁇ (EN 1993-1-2) 74705-031 20 1.000 1.000 1.00 400 1.000 1.000 1.00 500 0.872 0.780 1.12 600 0.655 0.470 1.39 700 0.419 0.230 1.82 800 0.140 0.110 1.27 900 0.061 0.060 1.02 15874-016 20 1.000 1.000 1.00 400 1.000 1.000 1.00 500 0.932 0.780 1.20 600 0.670 0.470 1.42 700 0.438 0.230 1.90 800 0.152 0.110 1.38 900 0.064 0.060 1.07
- Table 9 shows composition information of normalized plates and the niobium dissolution temperature NBDT
- Table 10 shows mechanical properties and strengthening potentials LP 50 and LP 95 of normalized plates.
- Plates 15874-016 and 15874-033 were normalized at 950°C that is very close to the dissolution temperature of niobium (NBDT) calculated according to the Dong formula 957°C. In practice, this leads to C sol and Nb sol being very close to the total carbon and niobium concentrations of the plates.
- Table 9 Composition information of normalized plates and dissolution temperature of niobium NBDT Plate Thickness mm Normalizing temperature Ti N N* NBDT C sol Nb sol °C ppm ppm ppm °C % % 15874-016 12 950 160 55 8 957 0.016 0.042 15874-033 20 950 160 55 8 957 0.016 0.042
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Description
- The invention relates to a method for selecting the composition of low-alloy steel, and for manufacturing a steel product, for applications exposed to high temperatures.
- The invention also relates to a low-alloy hot rolled or normalized steel for use in applications, where endurance to high temperatures and heat resistance is required, the steel having a carbon concentration of above 0.01 percent by weight. This steel may be called fireproof steel and it is preferably hot-rolled.
- The invention further relates to the use of the steel of the invention.
- A special feature of fireproof structural steel is that its strength at high temperatures caused by fire is higher than conventional structural steels. In conventional structural steels, the strength decreases essentially as temperature rises, because the movement of steel dislocations becomes easier due to increasing thermal activation. The strength of fireproof steel is less sensitive to temperature increases than that of conventional structural steel.
- In conventional fireproof structural steels, the movement of dislocations is made more difficult by alloying the steel with Mo, Cr, V, or Nb, for example, into the steel. These elements react with the carbon in the steel and form M-C clusters or MxCy precipitations, wherein M is Mo or Cr or V or Nb, and x and y are specific to different compounds. M-C clusters cause interactive solid solution hardening that is an effective hardening mechanism in heat-resistant steels. MxCy precipitations may already be in the steel in supply condition or they may be formed during the heating caused by fire.
- Published patent
JP2004339549 - Published patent
JP2002173733 - Published patent
JP2006241552 -
US patent application 2006/0063335 A1 discloses a high-strength fire-resistant low-alloy steel. Its fire-resistant properties are based on a relatively high molybdenum concentration and on the use of boron. The molybdenum concentration is preferably 0.2-1.1 wt % and boron 0.0005-0.003 wt %. Presumably the impact strength of the steel is not especially good, because the alloying of boron weakens it. Molybdenum also weakens the impact strength, and is also an expensive alloying element. -
WO 2006/093282 discloses a low alloy hot-rolled fire resistant steel and a method for manufacturing the same. - A drawback of the above patent publications is that they do not teach how to select a composition of fireproof steel and to manufacture a steel product to correspond to a desired yield strength grade in the strength range of 355 to 690 MPa and a desired fire-resistant property (by utilizing the strengthening potential of the steel that depends on the composition of the steel).
- An object of the invention is to provide a method with which the composition of steel may be selected to correspond to a desired fire-resistance and strength at high temperatures and a method for manufacturing a steel product having said composition. To achieve this, the method of the invention is characterised by
selecting the C, Si, Mn, Cr, Mo, Ni, Cu and B -level and the cooling rate (CR) of the steel after hot-rolling,
calculating the yield strength of the steel having the selected composition using the formula
C is the carbon concentration of the steel (wt %),
Si is the silicon concentration of the steel (wt %),
Mn is the manganese concentration of the steel (wt %),
Cr is the chromium concentration of the steel (wt %),
Mo is the molybdenum concentration of the steel (wt %),
Ni is the nickel concentration of the steel (wt %),
Cu is the copper concentration of the steel (wt %), and
BL refers to the boron level of the steel, and
BL = 0, if B ≤ 0.0005 and BL = 1, if B > 0.0008, wherein B is the boron concentration of the steel (wt %), and
CR refers to the cooling rate after hot-rolling (°C/s),
comparing the calculated yield strength with a desired yield strength grade specified for the application,
if the calculated yield strength satisfies the desired yield strength grade, calculating for the steel having said composition a strengthening potential, LP95, using the formula
Nb is the niobium concentration of the steel (wt %), and
if the calculated strengthening potential LP95 > 0, the steel having said composition is suitable to be used in the application; and
the method further comprising manufacturing the steel product using the selected composition and the selected cooling rate.
LP95 is the strengthening potential of the steel that provides an estimate on how much the yield strength of the steel (MPa) increases at room temperature, if steel is heated to a temperature of 600°C for one hour. In the stengthening potential formula C is the carbon concentration of the steel (wt %), when the steel is in the hot-rolled condition, and C is the carbon concentration in solution in austenite, Csol, at the normalizing temperature of the steel, when the steel is normalized steel, and
Nb is the niobium concentration of steel (wt %), when the steel is in the hot-rolled condition, and Nb is the niobium concentration in solution in austenite, Nbsol, at the normalizing temperature of the steel, when the steel is normalized steel. - The correctness of the strengthening potential has been tested to be approximately 95%, i.e., the room-temperature yield point of the steel heated to a temperature of 600 °C for one hour deducted by the yield point of the steel in delivery state will at a probability of 95% increase at least by the value LP95.
- In the invention, it was surprisingly detected that quite small alloying element concentrations produce good fire-resistance, when the alloying elements and their concentrations are selected correctly.
- The value of the strengthening potential LP95 is preferably selected to be above 50, whereby a steel has been selected having a good fire-resistance at high temperatures and a high strength reduction coefficient (the strength does not decrease much at high temperatures).
- It has been noted that niobium greatly increases fire-resistance which is why the niobium concentration of steel is preferably at least 0.04 wt %. Most preferably, the niobium concentration is 0.08-0.12 wt %. During hot-rolling of steel, niobium precipitates into niobium carbides, which results in a smaller grain size of steel, improved ductility and strength. Part of the niobium also precipitates into niobium carbides during the cooling after hot-rolling. However, part of the niobium remains in the solution when the carbon concentration of steel is very low, such as in the steel of the invention; the higher concentration of niobium, the more of it remains in solution. In case of fire, the niobium in solution joins the carbon of the steel and forms strengthening precipitations and clusters. As a result of this, the steel remains strong at temperatures caused by fire.
- Because carbon increases the strengthening potential to a significant extent, the carbon concentration is at least above 0.01 wt % and preferably above 0.03 wt %. The maximum value of the steel strengthening potential is reached at a carbon concentration of below 0.05 wt %, which is why the upper limit for carbon concentration is preferably selected to be 0.05 wt %. Another reason for preferably selecting 0.05% as the upper limit for carbon concentration is that the impact strength and weldability of the steel then remain good.
- Because (surprisingly) the molybdenum concentration of steel does not much increase the strengthening potential of steel, and molybdenum is also an expensive alloying element, the molybdenum concentration is preferably selected to be below 0.4 wt %.
- Preferably the composition of the steel is selected so that its composition in percent by weight is:
C: 0.01-0.05 Si: at most 0.7 Mn: 1.0-2.3 Ni: at most 1.5 Cr: at most 1.5 Mo: at most 0.7 Cu: at most 0.3 Nb: 0.04-0.15 B: at most 0.004 N: at most 0.01 Al: at most 0.1 V: at most 0.02 Ti: at most 0.05 Ca: at most 0.006, whereby - The greatest advantages of the method of the invention are that, at a general level, it facilitates the selection of the composition of steel and manufacturing of a steel product, for the purpose of obtaining steel with good fire-resistance properties, whereby the method also makes it possible to minimize alloying element costs. The method also facilitates the selection of the composition for the purpose of obtaining steel classified in various strength grades S355, S420, S460, S500, and S690 (the minimum values of yield strengths 355, 420, 460, 500, and 690 MPa). The steel is preferably a hot-rolled plate or strip, even though other delivery forms may also apply.
- Another object of the invention is to provide for use a fire-resistant low-alloy steel with good fire-resistance without needing to use high concentrations of expensive alloying elements in it. The steel is also easy to manufacture and weld.
- To achieve this, the steel is mainly characterised in that its composition in percentage by weight is as follows:
C: above 0.01 and at most 0.05 Si: at most 0.7 Mn: 1.0-2.3 Ni: at most 1.5 Cr: at most 1.5 Mo: < 0.4 Cu: at most 0.3 Nb: 0.04-0.15 B: at most 0.004 N: at most 0.01 Al: at most 0.1 V: at most 0.02 Ti: at most 0.05 Ca: at most 0.006, whereby - Mn > 1.6 or Mo < 0.1, if B > 0.0005, and
- the alloying level of the steel ST = 33.8C + 0.98Si + 1.15Mn + 0.47Cr + 2.32Mo + 0.85Ni + 0.47Cu + 1.16BL = 3.0-8.0, wherein BL = 0, if B ≤ 0.0005 and BL = 1, if B > 0.0008, and the composition of the steel meets the criterion
- Preferably -177 + 9000C - 115000C2 + 750Nb + 71 Mo + 33Ni - 36Cr > 50, whereby the fire resistance of the steel at high temperatures is especially good and the strength reduction coefficient is high (the strength does not decrease much at high temperatures).
- Preferably, the lower limit of the carbon concentration of the steel is 0.03 wt %, because carbon increases the strengthening potential significantly.
- When the upper limit of the carbon concentration of the steel is 0.05 wt %, the weldability of the steel still remains good regardless of the carbon equivalent.
- The niobium concentration of the steel is preferably 0.08-0.12 wt %.
- If the boron concentration of the steel is above 0.0005 wt %, it is advantageous for the impact strength of the steel that at the same time the manganese concentration is above 1.6 wt % and the molybdenum concentration is below 0.1 wt %.
- The molybdenum concentration of the steel is preferably below 0.4 wt %, even though the boron concentration of the steel ≤ 0.0005 wt %.
- Preferably N < 0.008 and 2 < Ti/N > 3, if B ≤ 0.0005 wt %.
- Preferably Ti/N > 3.4 or Al/N > 8, if B > 0.0005 wt %.
- Surprisingly, the reduction coefficient of the low-alloy steel of the invention at 700°C is significantly higher than the reduction coefficient presented in SFS standard EN 1993-1-2. Preferably, the reduction coefficient achievable for the steel is above 0.3 and more preferably above 0.4 at 700°C as measured using a transient test.
- Preferred embodiments of the steel according to the invention are disclosed in the attached claims 3 to 13.
- The greatest advantages of the steel according to the invention are that its fire resistance is good and the fire resistance is achieved with a small amount of expensive alloying elements. In addition, the steel can be easily and economically manufactured for yield strength grades 355, 420, 460, 500, and 690 MPa, and its composition is suitable for both thick and thin forms. The steel is preferably a hot-rolled plate or strip, even though other products or forms may also apply.
- The steel according to the invention is used in applications requiring high strength at temperatures above 400°C, even 600 to 800°C. Such applications include those in which the steel must be fire resistant. These typically include steel structures of buildings wherein the steel is preferably used in building beams and lattice structures. The building beams may for instance be welded double-web Q beams or single-web I beams, in which steel is used in the entire beam or only in parts significant for fire protection, such as the top or bottom flange. The steel of the invention works especially well for instance in situations where the intermediate floor slab system of a building is supported by a Q beam and the bottom or top flange of the beam is not protected by the slab system or concreting, whereby the flange requires especially good fire resistance. Other fire protection means are not needed when the required part of the beam is made of the steel of the invention.
- By using the steel of the invention in structures, it is possible to leave out traditional fire protection means, such as painting steel structures (wherein the paint is of a type that foams at high temperatures and therefore provides heat insulation), protecting steel structures by encasing them with gypsum boards or protecting them with rigid, heat-resistant, insulating wool.
- In the steel of the invention, molybdenum and boron are not necessary, even though they may be utilised (Mo: 0-0.7 wt %, preferably < 0.4 wt %, B: 0-0.0040 wt %). Manganese is an essential alloying element to provide strength and impact strength, which is why manganese is alloyed in 1-2.3 wt % depending on the boron concentration of the steel. It has been noted that in hot-rolled steel both molybdenum and boron reduce the impact strength of the steel, whereas by increasing the manganese concentration, the impact strength of the steels according to the invention improves. The effect of boron is great: the transition temperature of impact strength may increase as much as 50°C when boron is alloyed in steel. However, if the cost-effectiveness of boron as an alloying element is to be utilised by alloying above 0.0005 wt % of boron into the steel, the manganese concentration is selected to be above 1.6 wt % and/or (preferably and than or) the molybdenum concentration at most 0.1 wt%.
- In the steel of the invention, the proportions of bainite and ferrite in the microstructure are not restricted.
- The invention makes it possible to design steel structures with desired fire-resistance properties at manufacturing costs that are as economical as possible.
- The invention will now be described in greater detail by means of examples and with reference to the attached figure.
- When the intention is to obtain a fireproof steel meeting certain tensile properties, a steel is selected according to the invention by using the formula
C is the carbon concentration of the steel (wt %) when the steel is in the hot-rolled condition, and C is the carbon concentration in a solution in austenite, Csol, at the normalizing temperature of the steel, when the steel is normalized steel,
Nb is the niobium concentration of the steel (wt %), when the steel is in the hot-rolled condition, and Nb is the niobium concentration in solution in austenite, Nbsol, at the normalizing temperature of the steel, when the steel is normalized steel,
Mo is the molybdenum concentration of the steel (wt %),
Ni is the nickel concentration of the steel (wt %), and
Cr is the chromium concentration of the steel (wt %). - The correctness of the formula has been tested to be approximately 95%, i.e., the room-temperature yield point of the steel heated to a temperature of 600 °C for one hour deducted by the yield point of the steel in delivery state will at a probability of 95% increase at least by the value LP95.
- Preferably, LP95 > 50, and in applications requiring very high fire resistance, LP95 > 100 is selected.
- The effect of carbon on the strengthening potential is great, and this may also be observed from the attached figure that shows steel that contains not only carbon, but also 0.04 wt % of Nb, 0.14 wt % of Cr, 0.17 wt % of Mo, and 0.76 wt % of Ni. The LP50 marked in the curve refers to the strengthening potential that will be exceeded at 50% probability (LP50=LP95+55).
- The carbon concentration of the steel is at least 0.01 wt %. Preferably, the carbon concentration of the steel is above 0.03 wt % and at most 0.05 wt %, and its niobium concentration is 0.04-0.15 wt % and more preferably 0.08-0.12 wt %. The aim is to keep the molybdenum concentration relatively low due to the high price of molybdenum. The molybdenum concentration is preferably below 0.4 wt %, and if the steel contains above 0.0005 wt % of boron, the molybdenum concentration is below 0.1 wt %.
- The above formula and condition for the strengthening potential LP95 applies when the following conditions are met:
- 1) the steel is manufactured hot-rolled either in a plate or strip mill,
- 2) the heating temperature of a blank, TS, is higher than NBDT, i.e., niobium dissolution temperature (dissolution temperature of niobium carbonitrides), but at most 1300°C; it is even more preferable that the heating temperature of a blank, TS, is higher than NBDT by +50°C.
NBDT is calculated using the Dong formula: - 3) the finish rolling temperature FRT is higher than the formation temperature of ferrite, Ar3, and at most 1050°C.
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- Cooling after plate-rolling may take place freely in air or as accelerated cooling with water, for instance, as long as the cooling time from 750°C to 400°C is shorter than 5000 s which corresponds to the average cooling rate that is higher than 0.07°C/s at 750 to 400°C.
- After strip-rolling, the cooling must be accelerated with water to a temperature of 450°C or below.
- If heating temperatures of a blank, TS, below NBDT are used to obtain good impact strength, for instance, the same LP95 formula is used to calculate the strengthening potential, but the carbon and niobium concentrations refer to those in solution in austenite at the heating temperature of a blank, Csol and Nbsol, that is,
T1=TS, the heating temperature of a blank in Celsius. - If normalizing is performed after rolling, the LP95 formula may still be used as long as the normalizing temperature, Tn, exceeds NBDT. If Tn < NBDT, the LP95 formula uses carbon and niobium concentrations, Csol and Nbsol, that are at the normalization temperature in the solution. Csol and Nbsol are calculated using the above Dong formula by placing T1=Tn into the formula.
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- Table 2 shows compositions of steel plates according to the invention within the alloying element concentrations given in Table 1. Yield point and tensile strength values were measured for these steel plates, see Table 3.
Table 2: Chemical compositions of plates (wt %) Plate Thickness mm Type C % Si % Mn % Cu % Cr % Ni % Mo % Nb % B % BL ST 1142-1 / -2 12 miniature 0.024 0.17 1.99 0.22 0.03 0.82 0.26 0.054 0.0003 0 4.7 1143-1 / -2 12 miniature 0.043 0.18 1.99 0.23 0.03 0.81 0.26 0.054 0.0003 0 5.3 1144-1 / -2 12 miniature 0.011 0.19 1.98 0.22 0.03 0.82 0.26 0.052 0.0003 0 4.3 1145-1 / -2 12 miniature 0.040 0.18 2.08 0.21 0.03 0.13 0.11 0.103 0.0013 1 5.6 1146-1 / -2 12 miniature 0.022 0.17 2.09 0.22 0.03 1.01 0.11 0.048 0.0004 0 4.6 1147-1 / -2 12 miniature 0.015 0.18 1.36 0.22 0.03 0.13 0.61 0.044 0.0017 1 5.1 1148-1 / -2 12 miniature 0.040 0.18 1.33 0.22 0.03 1.02 0.61 0.112 0.0004 0 5.5 1149-1 / -2 12 miniature 0.016 0.19 2.08 0.22 0.99 0.13 0.60 0.101 0.0004 0 5.2 1150-1 / -2 12 miniature 0.015 0.17 1.35 0.21 0.99 1.02 0.11 0.100 0.0011 1 5.1 1151-1 / -2 12 miniature 0.041 0.19 1.36 0.22 1.00 0.13 0.11 0.048 0.0003 0 4.1 1152-1 / -2 12 miniature 0.040 0.20 2.09 0.23 1.00 1.00 0.61 0.046 0.0014 1 8.0 1180-1 / -2 12 miniature 0.029 0.19 1.60 0.21 0.03 0.02 0.00 0.042 0.0003 0 3.1 1181-1 / -2 12 miniature 0.028 0.68 1.91 0.22 0.03 0.80 0.24 0.048 0.0003 0 5.2 1182-1 / -2 12 miniature 0.036 0.21 2.43 0.22 0.82 0.32 0.00 0.043 0.0027 1 6.1 1183-1 / -2 12 miniature 0.047 0.23 2.02 0.22 0.91 0.99 0.48 0.062 0.0003 0 6.6 1184-1 / -2 12 miniature 0.037 0.22 2.02 0.23 0.91 0.51 0.10 0.097 0.0030 1 6.2 68816-023 120 normal 0.014 0.29 1.92 0.22 0.16 0.77 0.19 0.050 0.0001 0 4.3 74705-031 20 normal 0.016 0.26 2.13 0.20 0.18 0.78 0.20 0.049 0.0003 0 4.5 15874-016 12 normal 0.017 0.30 1.93 0.21 0.14 0.76 0.17 0.042 0.0003 0 4.3 15874-033 20 normal 0.017 0.30 1.93 0.21 0.14 0.76 0.17 0.042 0.0003 0 4.3 - Other alloying element concentrations are according to Table 1.
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- In the above formulas, C, Si, Mn, Cr, Mo, and Cu refer to the alloying element concentrations in percent by weight. C is the carbon concentration of the steel (wt %), when the steel is hot-rolled steel, and C is the carbon concentration in solution in austenite, Csol, at the normalization temperature of the steel, when the steel is normalized steel. BL refers to the boron level. If B ≤ 0.0005%, BL = 0; if B > 0.0008% BL = 1. (B concentrations of 0.0006 ... 0.0008% are not recommended, because the activity of boron is then uncertain.) CR refers to the average cooling rate at 750 to 400°C.
- The above formula predicting the yield strength is used when it is necessary to select steel that corresponds to a desired yield strength grade.
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- If the plate is made air-cooled, the cooling rate may be estimated on the basis of the thickness of the plate by using the following formula:
T0 is a first temperature on Kelvin scale (in this case 750 + 273 K),
T1 is a second temperature on Kelvin scale (in this case 400 + 273 K), and
t is the thickness of the plate in millimetres. - The correctness of the presented strengthening potential has been verified with both miniature plates and normal-size plates whose chemical compositions were according to Table 1 and manufacturing parameters within the above-mentioned limits. In this context, reference is made to Table 3 that shows the yield and tensile strengths of the plates after hot-rolling and cooling as well as their computational/predicted strengths. The miniature plates were made with a pilot roll to be 12 mm thick. After rolling, the miniature plates were cooled either freely in air or using accelerated cooling with water to room temperature as soon as possible after rolling. This way, cooling rates of 13 or 1.5°C/s were achieved at 750 to 400°C. Normal-size plates were 12 to 120 mm thick. They were rolled within the above-mentioned parameter limits. After rolling they were cooled either freely in air or using accelerated cooling with water to a temperature of 100 to 300°C. Table 3 shows that the predicted values are close to the measured values in both miniature and normal-size plates.
- Table 3 also proves that by selecting the composition and manufacturing parameters of the steel by using the limits and formulas of the invention, it is possible to manufacture plates for yield strength grades 420, 460, 500, or 690 MPa, for instance. The impact strength of the steel is also adjusted to the desired level by controlling the impurities contents (S, P, O, N), calcium processing, and rolling and cooling conditions.
Table 3: Yield and tensile strengths of the plates after hot-rolling and cooling (AR = as rolled) Plate Thickness mm CR °C/s Rp0.2(AR) measured Rp0.2(AR) predicted Rm(AR) measured Rm(AR) predicted Strength grade MPa 1142-1 12 13.0 544 563 703 707 500 1143-1 12 13.0 555 606 764 801 500 1144-1 12 13.0 525 535 642 644 500 1145-1 12 13.0 619 665 829 835 500 1146-1 12 13.0 525 562 687 706 500 1147-1 12 13.0 579 573 721 693 500 1148-1 12 13.0 590 559 779 771 500 1149-1 12 13.0 607 631 748 755 500 1150-1 12 13.0 585 601 752 795 500 1151-1 12 13.0 493 512 715 735 460 1152-1 12 13.0 809 836 1082 1068 690 1180-1 12 13.0 498 444 624 588 460 1181-1 12 13.0 581 606 760 763 500 1182-1 12 13.0 819 752 980 936 690 1183-1 12 13.0 816 714 1001 954 690 1184-1 12 13.0 771 723 982 933 690 1142-2 12 1.5 509 525 680 680 500 1143-2 12 1.5 532 568 740 749 500 1144-2 12 1.5 511 497 633 633 500 1145-2 12 1.5 563 565 780 773 500 1146-2 12 1.5 502 516 660 668 500 1147-2 12 1.5 549 531 692 709 500 1148-2 12 1.5 601 574 773 755 500 1149-2 12 1.5 599 585 751 730 500 1150-2 12 1.5 560 559 732 727 500 1151-2 12 1.5 446 525 644 633 420 1152-2 12 1.5 679 735 974 1012 500 1180-2 12 1.5 480 438 535 531 460 1181-2 12 1.5 585 574 732 729 500 1182-2 12 1.5 630 623 830 838 500 1183-2 12 1.5 730 673 897 882 690 1184-2 12 1.5 665 627 851 839 500 74705-031 20 12.0 569 571 660 693 500 15874-016 12 25.0 569 552 656 682 500 15874-033 20 11.0 571 539 644 670 500 68816-023 120 0.07 467 460 573 599 460 - Tables 2 and 3 show that the cooling rate does not much affect the strength properties of the plates at least when the cooling rates are low, so it is easy to use the presented strengthening potential formula to design compositions for fireproof steels in such a manner that it is possible to use the same composition to manufacture both thick and thin plates and strip plates. The examples of Table 3 show that a given strength grade may be manufactured of the same composition regardless of the cooling rate.
- Table 4 shows calculated strengthening potentials LP50 and LP95 and measured strength increases. It can be noted that in only two cases of thirty three the measured strengthening potential is lower than the LP95 prediction. The highest predicted LP95 value is 161 MPa that is achieved with the relatively high-alloy plate 1148.
Table 4: Calculated LP values in comparison with measured differences Rp0.2(1 h600°C)-Rp0.2(AR) Plate Thickness CR Rp0.2(AR) measured Rp0.2(1h600°C) measured Rm(1h600°C) measured Rp0.2(1h°600C)-Rp0.2(AR) measured LP50 LP95 mm °C/s MPa MPa MPa MPa MPa MPa 1142-1 12 13.0 544 677 735 133 114 59 1143-1 12 13.0 555 722 783 167 139 84 1144-1 12 13.0 525 545 620 20 47 -8 1145-1 12 13.0 619 792 847 173 144 89 1146-1 12 13.0 525 647 703 122 98 43 1147-1 12 13.0 579 661 755 82 67 13 1148-1 12 13.0 590 801 868 211 216 161 1149-1 12 13.0 607 683 754 76 80 25 1150-1 12 13.0 585 675 743 90 69 14 1151-1 12 13.0 493 626 704 133 67 12 1152-1 12 13.0 809 970 1011 161 131 76 1180-1 12 13.0 498 572 628 74 75 20 1181-1 12 13.0 581 704 782 123 120 65 1182-1 12 13.0 819 823 863 4 68 13 1183-1 12 13.0 816 954 1006 138 130 75 1184-1 12 13.0 771 872 932 101 119 64 1142-2 12 1.5 509 648 736 139 114 59 1143-2 12 1.5 532 678 786 146 139 84 1144-2 12 1.5 511 527 608 16 47 -8 1145-2 12 1.5 563 734 842 171 144 89 1146-2 12 1.5 502 619 703 117 98 43 1147-2 12 1.5 549 639 739 90 67 13 1148-2 12 1.5 601 780 867 179 216 161 1149-2 12 1.5 599 664 731 65 80 25 1150-2 12 1.5 560 651 724 91 69 14 1151-2 12 1.5 446 531 623 85 67 12 1152-2 12 1.5 679 805 965 126 131 76 1180-2 12 1.5 480 488 544 8 75 20 1181-2 12 1.5 585 675 773 90 120 65 1182-2 12 1.5 630 688 792 58 68 13 1183-2 12 1.5 730 807 937 77 130 75 1184-2 12 1.5 665 766 884 101 119 64 74705-031 20 12.0 569 613 670 44 63 8 15874-016 12 25.0 569 591 652 22 63 8 15874-033 20 11.0 571 589 648 18 63 8 68816-023 120 0.1 467 484 574 17 53 -2 - Table 5 shows the chemical composition of three comparison steels.
Table 5: The chemical composition of three comparison materials (wt %) Plate Thickness mm CR °C/s C % Si % Mn % Al % Nb % V % Ti % Cr % Cu % Ni % Mo % N % B % 41278-024 30 0.3 0.12 0.35 1.56 0.040 0.037 0.004 0.005 0.02 0.01 0.04 0.00 0.0068 0.0002 50902-013 20 0.4 0.14 0.36 1.50 0.042 0.040 0.039 0.017 0.02 0.01 0.48 0.00 0.0099 0.0003 14630-034 20 16 0.08 0.16 1.51 0.035 0.037 0.005 0.017 0.02 0.28 0.76 0.00 0.0060 0.0003 - Plates 41278-024 and 50902-013 were cooled freely in air. Plate 14630-034 was cooled accelerated at 750-550°C.
- Table 6 shows the mechanical properties of comparison steels rolled and after heat treatment. The table shows that the measured strengthening potentials, ReH(AR) - ReH(1h600°C) that correspond to the LP50 value, are typically negative. The comparison steels have clearly higher carbon concentrations than the steels of the invention, and on the basis of the LP95 formula, it is expected that EP decreases when the carbon concentration increases above approximately 0.040%.
Table 6: The mechanical properties of comparison materials rolled and after heat treatment Plate Thick CR Rolled Heat treated 600°C ReH(600°C)-ReH(AR) mm °C/s ReH MPa Rm MPa A5 % Temp °C Time min ReH MPa Rm MPa A5 % MPa 41278-024 30 0.3 455 557 30 600 60 445 553 32 -10 50902-013 20 0.4 503 642 24 600 40 501 623 24 -2 14630-034 20 16 577 685 14 600 40 572 657 21 -5 - The fire-resistance of the plates of the invention was tested in transient tests. Their mechanical properties in delivery state are shown in Table 7.
Table 7: The mechanical properties of plates tested in transient tests Plate No. Thickness Cooling rate As rolled Heat-treated 1h600°C Charpy V as rolled crosswise, -60 °C Rp0.2 Rm A Rp0.2 Rm A mm °C/s MPa MPa % MPa MPa % J 74705-031 20 12 569 660 22 613 670 23 310 15874-016 12 25 569 656 21 591 652 22 207 15874-033 20 11 571 644 21 589 648 23 271 - Table 8 shows the strength properties measured by transient tests at high temperatures for the steel plates of the invention and conventional structural steels. In transient tests, the strength of the material (steel) is measured in hot tensile tests, wherein a piece of steel is loaded in a test furnace at different tensile loads by increasing the temperature from 20°C to 900°C at the same time. Yield strength values at different temperatures are measured for the material (steel) on the basis of the load tests. Yield strength is the level of stress at a selected elongation value. The fire resistance of the plates made according to the invention has been tested in transient tests according to the standard EN 10002-5. A transient test is suitable when there is a need to define the strength properties of the material in fire conditions.
-
- Table 8 shows that the fire properties of the steel plates of the invention are clearly better than those of conventional structural steels: at 700°C, the reduction coefficient of the effective yield point is 82 to 90% higher in the steel of the invention than in conventional steel. The reduction coefficient of the steels of the invention is above 0.3 and preferably above 0.4 at 700°C, which values can be seen to be true, see Table 8.
Table 8: Strength properties measured by transient tests at high temperatures Plate of the invention Temperature Measured reduction coefficient Reduction coefficient SFS EN 1993-1-2 Ratio °C ky,θ(measured) ky,θ(EN 1993-1-2) ky,θ(measured) / ky,θ(EN 1993-1-2) 74705-031 20 1.000 1.000 1.00 400 1.000 1.000 1.00 500 0.872 0.780 1.12 600 0.655 0.470 1.39 700 0.419 0.230 1.82 800 0.140 0.110 1.27 900 0.061 0.060 1.02 15874-016 20 1.000 1.000 1.00 400 1.000 1.000 1.00 500 0.932 0.780 1.20 600 0.670 0.470 1.42 700 0.438 0.230 1.90 800 0.152 0.110 1.38 900 0.064 0.060 1.07 - Table 9 shows composition information of normalized plates and the niobium dissolution temperature NBDT, and Table 10 shows mechanical properties and strengthening potentials LP50 and LP95 of normalized plates. Plates 15874-016 and 15874-033 were normalized at 950°C that is very close to the dissolution temperature of niobium (NBDT) calculated according to the Dong formula 957°C. In practice, this leads to Csol and Nbsol being very close to the total carbon and niobium concentrations of the plates. The calculated LP values (LP50 = 58 MPa and LP95 = 3 MPa) are well in concordance with the measured strengthening potentials (75 and 69 MPa), so the strengthening potential formulas of the invention may also be used to make normalized fireproof steel. The examples of Tables 9 and 10 show that by using the above formulas and normalization heat-treatment, it is also possible to manufacture fireproof steels in the yield strength grade of 355 MPa.
Table 9: Composition information of normalized plates and dissolution temperature of niobium NBDT Plate Thickness mm Normalizing temperature Ti N N* NBDT Csol Nbsol °C ppm ppm ppm °C % % 15874-016 12 950 160 55 8 957 0.016 0.042 15874-033 20 950 160 55 8 957 0.016 0.042 - Other alloying element concentrations are given in Tables 1 and 2. N* = N - Ti/3.42
Table 10: Mechanical properties and precipitation potentials of normalized plates (as-rolled mean) Plate No. Thickness NBDT As rolled Heat-treated 1h600°C Measured strengthening potential Rp0.2(1h600°C)-Rp0.2(AR) Calculated mm °C Rp0.2 Rm A Rp0.2 Rm A LP50 LP95 MPa MPa % MPa MPa % MPa MPa MPa 15874-016 12 952 383 544 29 458 548 29 75 58 3 15874-033 20 952 398 554 28 467 561 29 69 58 3 - Above the invention has been illustrated by means of examples. In detail the invention may be implemented in many ways within the scope of the attached claims.
Claims (13)
- A method for manufacturing a steel product, the method comprising selecting a low-alloy hot-rolled or normalized steel for applications exposed to high temperatures, characterised by
selecting the C, Si, Mn, Cr, Mo, Ni, Cu and B -level and the cooling rate (CR) of the steel after hot-rolling,
calculating the yield strength of the steel having the selected composition using the formula
C is the carbon concentration of the steel (wt %),
Si is the silicon concentration of the steel (wt %),
Mn is the manganese concentration of the steel (wt %),
Cr is the chromium concentration of the steel (wt %),
Mo is the molybdenum concentration of the steel (wt %),
Ni is the nickel concentration of the steel (wt %),
Cu is the copper concentration of the steel (wt %), and
BL refers to the boron level of the steel, and
BL = 0, if B ≤ 0.0005 and BL = 1, if B > 0.0008, wherein B is the boron concentration of the steel (wt %), and
CR refers to the cooling rate after hot-rolling (°C/s),
comparing the calculated yield strength with a desired yield strength grade specified for the application,
if the calculated yield strength satisfies the desired yield strength grade, calculating for the steel having said composition a strengthening potential, LP95, using the formula
wherein Nb is the niobium concentration of the steel (wt %), and
if the calculated strengthening potential LP95 > 0, the steel having said composition is suitable to be used in the application; and
the method further comprising manufacturing the steel product using the selected composition and the selected cooling rate. - A method as claimed in claim 1, characterised in that the composition of the steel is selected so that its composition in percent by weight is:
C: 0.01-0.05 Si: at most 0.7 Mn: 1.0-2.3 Ni: at most 1.5 Cr: at most 1.5 Mo: at most 0.7 Cu: at most 0.3 Nb: 0.04-0.15 B: at most 0.004 N: at most 0.01 Al: at most 0.1 V: at most 0.02 Ti: at most 0.05 Ca: at most 0.006, whereby
the alloying level of the steel ST = 33.8C + 0.98Si + 1.15Mn + 0.47Cr + 2.32Mo + 0.85Ni + 0.47Cu + 1.16BL so that its value is 3.0-8.0, wherein BL = 0, if B ≤ 0.0005 and BL = 1, if B > 0.0008. - A low-alloy hot-rolled or normalized steel for use in applications requiring endurance of high temperatures and heat resistance, the carbon concentration of the steel being > 0.01 wt %, characterised in that the composition of the steel in percent by weight is as follows:
C: above 0.01 and at most 0.05 Si: at most 0.7 Mn: 1.0-2.3 Ni: at most 1.5 Cr: at most 1.5 Mo: < 0.4 Cu: at most 0.3 Nb: 0.04-0.15 B: at most 0.004 N: at most 0.01 Al: at most 0.1 V: at most 0.02 Ti: at most 0.05 Ca: at most 0.006, whereby
the alloying level of the steel ST = 33.8C + 0.98Si + 1.15Mn + 0.47Cr + 2.32Mo + 0.85Ni + 0.47Cu + 1.16BL = 3.0 - 8.0, wherein BL = 0, if B ≤ 0.0005 and BL = 1, if B > 0.0008, and the composition of the steel meets the criterion - A steel as claimed in claim 3, characterised in that -177 + 9000C - 115000C2 + 750 Nb + 70Mo + 33Ni - 36Cr > 50.
- A steel as claimed in claim 3, characterised in that -177 + 9000C - 115000C2 + 750 Nb + 70Mo + 33Ni - 36Cr > 100.
- A steel as claimed in any one of preceding claims 3 to 5, char- acterised in that the carbon concentration of the steel is at least 0.03 wt %.
- A steel as claimed in any one of the preceding claims 3 to 6, characterised in that the niobium concentration of the steel is 0.08-0.12 wt %.
- A steel as claimed in any one of the preceding claims 3 to 7, characterised in that B ≤ 0.0005, N < 0.008 and 2 <Ti/N < 3.
- A steel as claimed in any one of the preceding claims 3 to 7, characterised in that the steel is boron-free.
- A steel as claimed in any one of the preceding claims 3 to 7, characterised in that Ti/N > 3.4 or Al/N > 8, if B > 0.0005.
- A steel as claimed in any one of the preceding claims 3 to 10, characterised in that the reduction coefficient of its strength at 700°C is > 0.3 measured in a transient test.
- The use of a steel according to any one of the preceding claims 3 to 11 in applications that require high strength at temperatures above 400°C.
- The use of the steel according to claim 12 in building beams.
Priority Applications (1)
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PL08856442T PL2235226T3 (en) | 2007-12-07 | 2008-12-05 | Method for selecting composition of steel and its use |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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FI20075886A FI20075886L (en) | 2007-12-07 | 2007-12-07 | Procedure for selecting consistency of steel, steel and use of same |
PCT/FI2008/050715 WO2009071752A1 (en) | 2007-12-07 | 2008-12-05 | Method for selecting composition of steel and its use |
Publications (2)
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EP2235226A1 EP2235226A1 (en) | 2010-10-06 |
EP2235226B1 true EP2235226B1 (en) | 2014-04-09 |
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EP08856442.2A Not-in-force EP2235226B1 (en) | 2007-12-07 | 2008-12-05 | Method for selecting composition of steel and its use |
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EP (1) | EP2235226B1 (en) |
FI (1) | FI20075886L (en) |
PL (1) | PL2235226T3 (en) |
WO (1) | WO2009071752A1 (en) |
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CN116695023B (en) * | 2023-05-30 | 2024-08-16 | 鞍钢股份有限公司 | Steel for ultrahigh-strength and high-toughness low-yield-ratio longitudinal variable-thickness weather-resistant bridge and manufacturing method thereof |
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JPH10204573A (en) * | 1997-01-24 | 1998-08-04 | Nippon Steel Corp | 700×c fire resistant rolled shape steel and its production |
JP4860071B2 (en) | 2000-09-28 | 2012-01-25 | 新日本製鐵株式会社 | 800 ° C high-temperature fireproof building structural steel and method for producing the same |
US6841825B2 (en) | 2002-06-05 | 2005-01-11 | Shindengen Electric Manufacturing Co., Ltd. | Semiconductor device |
JP4031730B2 (en) | 2003-05-14 | 2008-01-09 | 新日本製鐵株式会社 | Structural 490 MPa class high-strength refractory steel excellent in weldability and gas-cutting property and method for producing the same |
JP4718866B2 (en) | 2005-03-04 | 2011-07-06 | 新日本製鐵株式会社 | High-strength refractory steel excellent in weldability and gas-cutting property and method for producing the same |
-
2007
- 2007-12-07 FI FI20075886A patent/FI20075886L/en not_active Application Discontinuation
-
2008
- 2008-12-05 PL PL08856442T patent/PL2235226T3/en unknown
- 2008-12-05 EP EP08856442.2A patent/EP2235226B1/en not_active Not-in-force
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Also Published As
Publication number | Publication date |
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FI20075886A0 (en) | 2007-12-07 |
FI20075886L (en) | 2009-06-08 |
EP2235226A1 (en) | 2010-10-06 |
PL2235226T3 (en) | 2014-09-30 |
WO2009071752A1 (en) | 2009-06-11 |
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