EP3084030B1 - Hohlprofil aus hochfestem warmgefertigtem stahl mit niedrigem kohlenstoffäquivalent für verbessertes schweissen - Google Patents
Hohlprofil aus hochfestem warmgefertigtem stahl mit niedrigem kohlenstoffäquivalent für verbessertes schweissen Download PDFInfo
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- EP3084030B1 EP3084030B1 EP14823925.4A EP14823925A EP3084030B1 EP 3084030 B1 EP3084030 B1 EP 3084030B1 EP 14823925 A EP14823925 A EP 14823925A EP 3084030 B1 EP3084030 B1 EP 3084030B1
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- 229910000831 Steel Inorganic materials 0.000 title claims description 52
- 239000010959 steel Substances 0.000 title claims description 52
- 238000003466 welding Methods 0.000 title claims description 14
- 229910052799 carbon Inorganic materials 0.000 title description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title description 17
- 238000001816 cooling Methods 0.000 claims description 33
- 238000005096 rolling process Methods 0.000 claims description 16
- 239000011575 calcium Substances 0.000 claims description 14
- 229910052791 calcium Inorganic materials 0.000 claims description 11
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 9
- 230000008569 process Effects 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 claims description 7
- 238000011282 treatment Methods 0.000 claims description 7
- 238000005266 casting Methods 0.000 claims description 6
- 238000003303 reheating Methods 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 239000002244 precipitate Substances 0.000 description 25
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 14
- 229910001566 austenite Inorganic materials 0.000 description 14
- 229910052720 vanadium Inorganic materials 0.000 description 13
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 13
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 229910000859 α-Fe Inorganic materials 0.000 description 10
- 239000011572 manganese Substances 0.000 description 9
- 239000002245 particle Substances 0.000 description 9
- 239000011651 chromium Substances 0.000 description 7
- 239000010949 copper Substances 0.000 description 7
- 229910052757 nitrogen Inorganic materials 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 239000004411 aluminium Substances 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 6
- 239000010955 niobium Substances 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 4
- 239000005864 Sulphur Substances 0.000 description 4
- 238000007792 addition Methods 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000011574 phosphorus Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000001627 detrimental effect Effects 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 239000010419 fine particle Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 238000009740 moulding (composite fabrication) Methods 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- AGVJBLHVMNHENQ-UHFFFAOYSA-N Calcium sulfide Chemical compound [S-2].[Ca+2] AGVJBLHVMNHENQ-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 150000004645 aluminates Chemical class 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- -1 calcium aluminates Chemical class 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000001427 coherent effect Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 239000003623 enhancer Substances 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- VCTOKJRTAUILIH-UHFFFAOYSA-N manganese(2+);sulfide Chemical class [S-2].[Mn+2] VCTOKJRTAUILIH-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000009659 non-destructive testing Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000011946 reduction process Methods 0.000 description 1
- 150000004760 silicates Chemical class 0.000 description 1
- 238000004513 sizing Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 239000000161 steel melt Substances 0.000 description 1
- 150000004763 sulfides Chemical class 0.000 description 1
Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
Definitions
- This invention relates to a high-strength hot-finished steel hollow section with low carbon equivalent for improved welding and a method for producing said section.
- Hot finished steel hollow sections are used in structural applications owing to their stable and uniform properties over the whole section. Hollow sections are e.g. known from JP 2001-262275A . Increasing the strength of the section allows either less material to be used in the same application, or more complicated design problems to be solved. Increasing the strength of steel typically leads to increasing the carbon equivalent level, which in turn leads to reduced performance in and upon welding, and can require special and more costly welding practices to be employed.
- hollow sections For hot-finished structural hollow sections of non-alloy and fine grain structural steels the relevant European standard is EN10210-1:2006.
- hollow sections can be supplied with a square, rectangular, circular or elliptical cross-section.
- the wall thickness varies as well as the external dimensions of the section.
- the section according to the invention offers a hot-finished steel hollow section that meets the S420 (EN10210-1:2006) industry standard for mechanical properties whilst also meeting the carbon equivalent maximum of the hot finished S355 standard which represents an 18% increased minimum yield strength level for the same carbon equivalent level.
- the invention achieves the required strength level in the hot formed condition by careful control of steel composition and processing steps.
- Cold formed hollow sections do not have uniform grain sizes and have greater brittleness in the corners or seam welded zones, leading to reduced performance in like-for-like hollow sections.
- cold formed hollow sections have a need for larger corner radii than hot-formed sections to prevent corner cracking.
- Cold formed and heat treated hollow sections offer improved performance over solely cold formed, but still do not offer the uniform grain size, hardness and tensile properties of a hot formed tube.
- Other hot finished hollow sections of which there are few in the market, offer a higher carbon equivalent level, which means reduced performance in and upon welding, and will require special and more costly welding practices to be employed.
- the final hot formed microstructure To achieve the required strength after hot forming whilst maintaining a low CEV for good weldability requires the final hot formed microstructure to have a fine ferrite grain size, a harder second phase such as pearlite or bainite, and fine precipitates such as vanadium carbonitrides (V(CN)) to give additional strength.
- the fine precipitates are vital, the required minimum yield strength of 420 MPa cannot be achieved by grain refinement alone if low CEV is to be maintained.
- the fine ferrite grain size is also vital in achieving good Charpy toughness.
- section according to the invention offers a hot-finished steel hollow section that meets the S420NH as well as the S420NLH standard, which indicates that the section has excellent impact properties at -20 and -50 °C.
- VN particles are effective in achieving this, as they retain a small size, and small particles are most efficient at pinning grain boundaries. It has been found that AlN particles are not as effective as VN, since AlN particles are larger. To obtain the appropriate fraction of VN particles requires the appropriate amount of vanadium and nitrogen and levels required are significantly higher than those used for conventional grades.
- the fine austenite grains whose boundaries are pinned by VN particles subsequently transform to fine ferrite grains on cooling through the transformation.
- V(CN) As well as a fine grain size, additional precipitation strengthening is required by fine particles.
- the VN particles which pin the austenite grain boundaries are too large to make a significant contribution, and will have lost coherency with the matrix due to the transformation and their size.
- Fine particles based on V(CN) are suitable to give this additional precipitation strengthening, also because these are (semi-)coherent precipitates.
- At the hot forming temperature some vanadium combines with nitrogen to form VN for austenite grain boundary pinning, but if the appropriate level of vanadium is chosen, some vanadium remains in solution at the hot forming temperature, and then precipitates as fine V(CN) precipitates during cooling, which make an important contribution to final strength.
- An appropriate carbon content is required to form sufficient V(CN) precipitates.
- carbon As well as reacting with vanadium to form V(CN), carbon also makes a contribution to strength via the formation of other second phases such as pearlite. However, if carbon is too high, the CEV will increase and reduce weldability. Similarly, increasing carbon decreases Charpy toughness, and there is a requirement for high Charpy toughness in the final product.
- the carbon content is therefore limited between 0.12 and 0.18 % (all compositional percentages are given in weight percent (wt.%) unless indicated otherwise). Preferably the carbon content is at least 0.13%. A suitable maximum carbon content was found to be 0.16%.
- a vanadium content of 0.13 to 0.20% is necessary.
- a preferable minimum vanadium content was found to be at least 0.15% or even at least 0.16%.
- a suitable maximum vanadium content was found to be at most 0.19% or even at most 0.18%.
- AlN forms in preference to VN, and AlN is not as efficient at pinning austenite grain boundaries as VN due to its larger size. Consequently the aluminium soluble (Al_sol) content is below 0.04%.
- the total aluminium content may be slightly higher due to the presence of e.g. alumina or aluminates. Preferably the aluminium content is at most 0.035%. A suitable minimum aluminium content was found to be 0.005%.
- Titanium content must be kept low, as titanium preferentially reacts with N, to form TiN rather than VN. These TiN-precipitates are not as effective as VN in pinning austenite grain boundaries. Moreover, TiN-precipitates are cuboids which may act as stress enhancers which may be undesirable in constructions which are stressed under conditions favourable to induce fatigue cracking. Consequently the titanium content is below 0.01%.
- Silicon adds strength without having a detrimental effect on weldability, but high silicon levels can have a detrimental effect on the ability to galvanise the steel, so the preference is for low silicon ( ⁇ 0.25%).
- High silicon additions result in thick layers of Fe-Zn compounds after galvanising which can be brittle.
- a suitable minimum silicon addition is 0.10%.
- the silicon content is at least 0.15% and/or at most 0.25%.
- Manganese is a useful strengthening element, and also contributes to grain refinement by lowering the austenite to ferrite transformation temperature. However, high levels of manganese do result in high CEV levels, which reduces weldability. For these reasons the manganese content is limited between 1.2 and 1.6%. Preferably the minimum content for manganese is 1.3%, more preferably at least 1.35%. A suitable maximum manganese content is 1.5%.
- Phosphorus and sulphur must be controlled to low levels to allow good Charpy toughness and weldability to be achieved, and to allow defect free slabs to be produced for rolling to strip.
- Phosphorus is therefore limited to at most 0.035% and sulphur to at most 0.015%.
- Phosphorus is therefore limited to at most 0.025% and/or sulphur to at most 0.008%.
- Nitrogen is an important element in that it participates in the reduction of the austenite grain size, and thus in that of the ferrite grain size, as well as in the precipitation hardening of the ferrite.
- a nitrogen content between 0.008 and 0.025% (i.e. 80 to 250 ppm) is needed for this purpose. Lower nitrogen levels result in an insufficient degree of precipitation and grain size control and higher levels require unfeasibly high slab reheating temperatures.
- the minimum content is 0.010 (100 ppm).
- a suitable maximum nitrogen content is 0.022 (220 ppm), preferably 0.020 % (200 ppm).
- CEV C + Mn 6 + Cr + Mo + V 5 + Cu + Ni 15
- the CEV must be kept low and below 0.45, so that weldability is equivalent to (i.e. just as good as) that of lower strength hollow sections.
- a low CEV means that additional weld processing steps such as pre-heating can be avoided, thus reducing fabrication costs.
- Nb(CN) particles will be present during the hot forming operation which will help to pin austenite grain boundaries, and hence promote a fine grain size in the final transformed ferritic product.
- solubility of Nb(CN) is less than that of V(CN), and insufficient niobium is in solution at the hot forming temperature to form fine precipitates during cooling which could contribute to strength.
- the addition of niobium enhances the susceptibility to the formation of cracks during continuous casting, so the addition must be done selectively.
- Chromium, nickel, molybdenum and copper may be used in the steel, provided the CEV stays below the threshold value. Since these elements affect the CEV as defined above directly, it is preferred to keep the amounts for these elements low. Chromium should be below 0.15, nickel and copper both below 0.20, and Molybdenum below 0.04. Preferably chromium and/or nickel and/or copper are below 0.05%. Preferably chromium, nickel and copper are each below 0.05%, and/or at most 0.10% jointly.
- the calcium treatment of aluminium-killed steels leads to the modification of non-metallic inclusions and the change of their chemical composition and plastic deformability.
- Calcium treatment has the benefit of modifying inclusion composition, and the shape and size of these inclusions are also adjusted.
- Two of the main advantages of calcium treatment are not only the improvement of the castability (prevention of clogging) but also the improvement of the final properties of the steels' machinability, toughness and surface quality.
- the effects of calcium are mainly based on its strong ability to form sulphides and oxides.
- the inclusion population will generally include alumina inclusions and maybe some silicates and manganese sulphides.
- the inclusions are restricted mainly to calcium aluminates (CaO-Al 2 O 3 ) and the sulphur in the steel is associated with these inclusions as calcium sulphide.
- the calcium levels in the final steel are low, and preferably below Ca ⁇ 0.015%, more preferably below 0.005.
- calcium is present in the steel as an alloying element (i.e. deliberately added), even though the amounts are minute, and not as an impurity (i.e. unavoidably present).
- the wall thickness of the section is at most 40 mm.
- the thickness range over which the section according to the invention satisfies the S420 industry standard is very wide.
- the EN10210 prescribes a yield strength of at least 400 MPa at a thickness above 16 mm. This value of at least 400 MPa is also met with the section according to the invention.
- the wall thickness of the section is at most 16 mm.
- the EN10210 requirement for yield strength of at least 420 MPa is met.
- the process for producing the steel hollow section is directed primarily to the hollow section as produced by hot rolling, forming, welding and heat treating, the inventors surprisingly found that the same chemistry can be advantageously used to produce steel hollow sections by means of a seamless production route wherein the hollow section is produced seamlessly and heat treated. Also for these sections the weldability is of great importance, as well as the mechanical properties.
- the slab casting process can be the thick slab casting process, resulting in slabs having a thickness above 150 mm, or the thin slab casting or thin slab casting and direct rolling process, resulting in slabs having a thickness below 150 mm, and generally having a thickness between 50 and 100 mm.
- Hot-rolling is therefore performed by rolling the steel slab to a hot-rolled strip with a finish rolling temperature in the range 800-950 °C, i.e. when the hot-rolling process is executed while the steel is fully austenitic;
- the fine ferrite grain size in the hot rolled strip is achieved by control of finish rolling temperature (FRT) in the austenite region, the use of water sprays to increase the cooling rates on the run out table between finish rolling and coiling, and by the selection of an appropriate coiling temperature.
- FRT finish rolling temperature
- the hot rolled strip is hard and difficult to cold form. If the coiling temperature is too high, a large ferrite grain size can result, and coarse AlN and V(CN) precipitates, which make achieving the required fine austenite grain size during hot forming difficult.
- the hot-forming temperature of the tube blank has to be carefully controlled. If the temperature is too low, then the tube blank is not completely transformed to austenite and vanadium is not dissolved to the appropriate extent. If the hot forming temperature is too high, then a large grain size will be formed, together with undesirable microstructures such as Widmann Toon ferrite, which will result in poor strength and toughness.
- the coiling temperature of the hot rolled strip is at least 560 °C and/or at most 650 °C.
- the upper boundary helps in achieving a fine microstructure, and the lower boundary helps to avoid harder microstructural components such as bainitic or even martensitic components.
- the cooling of the final hollow section to ambient temperature occurs by still air cooling, or by forced air cooling.
- the maximum cooling rate depends mainly on the steel grade.
- the occurrence of (small) islands of martensite in the final microstructure needs to be prevented to prevent a drop in yield strength.
- the average cooling rate between 850 and 550 °C is preferably at most 10 °C/s.
- Preferably the average cooling rate is at most 7.5 °C/s and more preferably at most 5 °C/s.
- coiled strip is slit to the required width, and the front end of the new coil is joined to the back end of the previous coil (e.g.) by a flash butt weld or MIG welding to produce a continuous length.
- the continuous strip is then passed through the forming mill, where a series of rolls form the strip into the required shape.
- High frequency electric resistance induction welding completes the formation of the tube.
- the external weld bead is removed, and the weld area is water cooled.
- the tube then passes through in line non-destructive testing, and is then sized to produce the required diameter and cut to length.
- EWSR Electric Weld Stretch Reduction
- Lengths of tube up to 120m long are heated to 900-1050 °C depending on the steel grade.
- the tubes are then passed through a series of roll stands in which they are stretch reduced to the required size and thickness.
- the sections are then cut to length, and placed on cooling racks, where continuous turning ensures uniform cooling.
- EW tubes that are to be hot finished and are not stretch reduced to achieve the final size are passed into a furnace where they are heated to a temperature between 850-1000 °C, and then hot rolled into their final profile after which they are allowed to cool.
- EW Electric Weld
- billets are reheated typically to temperatures in the range 1150-1250 °C, and then pierced.
- the pierced billet is then rolled to reduce the outside diameter and wall thickness.
- the tube may then pass through a final sizing mill, or in some processes be reheated again prior to passing through a stretch-reduction mill to achieve the final dimensions.
- the seamless tube may now be given further heat treatments, including heating in the range 850-1000 °C, to achieve the required final mechanical properties.
- Table 1 the results of steels 19 to 27 are presented, wherein steels 23 and 24 are comparative examples.
- Table 1 - results of steels 19 to 27 ID Type YS (MPa) TS (MPa) Elongation A (%) Charpy at - 20°C (J) 23 Comparison 414 554 31 214 24 Comparison 400 567 30 163 19 Invention 441 570 29 192 20 Invention 453 597 29 208 21 Invention 423 572 30 165 25 Invention 430 560 32 208 26 Invention 455 585 29 190 27 Invention 441 567 30 204
- L 0 is defined as 5.651 ⁇ (S 0 ), where S 0 is the surface of the cross section of the tensile specimen. E.g. for a round tensile specimen with a diameter of 8 mm, the gauge length is 40 mm.
- the TEM examination of carbon extraction replicas taken from samples quenched from the normalising temperature indicates the presence of VN precipitates and AlN precipitates.
- the VN precipitates mostly had a spherical or cuboid shape, but occasionally a larger, plate-like morphology was observed.
- the spherical and cuboid VN precipitates were mostly distributed in a random fashion, but occasionally short rows of precipitates were observed.
- the AlN precipitates were usually in the shape of rods or thin, angular prisms, and were much larger in size than the VN precipitates (typical AlN precipitates are about 100 nm in diameter, whereas the VN-precipitates are about 10nm in diameter) . They were usually arranged in short rows or clusters. Typical examples of precipitation in the base steel are shown in Figure 3a (AlN-precipitates) and b (VN-precipitates).
- the rolling conditions to produce the hot-rolled strip to be processed in the hollow section mills for the results presented in Table 2 were similar to those in table 1.
- the hot-rolled strip is processed into hollow sections in Tata Steel's Electric Weld Stretch Reduction mill (EWSR), and in Tata Steel's Electric Weld mill (EW).
- Figure 4 shows a schematic image of the production process.
- Table 3 results are given for steel 28, which has been processed as seamless tube of 12mm wall thickness, and then heat treated at temperatures in the range 880-1000 °C.
- Table 3 - results of steels 28 ID Normalising temperature, °C YS (MPa) UTS (MPa) A (%) A9 880 438 544 30.7 A11 920 439 559 31.7 A13 960 476 563 30.7 A14 980 478 571 30.3 A15 1000 494 584 30.0
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Claims (15)
- Hohlprofil aus hochfestem warmgefertigten Stahl mit niedrigem CEV, wobei CEV= C+(Mn/6)+((Cr+Mo+V)/5)+((Cu+Ni)/15), und wobei (in Gew.-%)• C: 0,12-0,18;• Si: < 0,60;• Mn: 1,2-1,6;• P: < 0,035;• S: < 0,015;• V: 0,13-0,20;• Al: < 0,04;• N: 0,008-0,025;• Ti: < 0,01;• Cr: < 0,15;• Ni: < 0,20;• Mo: < 0,04;• Cu: < 0,20;• Nb: < 0,05%• Wahlweise Ca < 0,015 %, vorzugsweise unter 0,005, in einer Menge, die einer Kalziumbehandlung zur Kontrolle von Einschlüssen entspricht;• Rest aus Eisen und unvermeidbaren Verunreinigungen;wobei CEV ≤ 0,45 %, und wobei die mechanischen Eigenschaften den Industrienormen S420NH und S420NLH gemäß EN10210-1:2006 entsprechen.
- Profil nach Anspruch 1, wobei Si ≤ 0,25 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei Si ≥ 0,10 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei V ≥ 0,15 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei V ≤ 0,19 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei eines oder mehrere von Cr, Ni und Cu zusammen höchstens 0,05 % und/oder höchstens 0,10 % sind.
- Profil nach einem der vorhergehenden Ansprüche, wobei CEV ≤ 0,44 %, vorzugsweise ≤ 0,435 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei• C: 0,13-0,16 % und/oder• Si: 0,15-0,25 % und/oder• Mn: 1,3-1,5 % und/oder• P: < 0,025 % und/oder• S: < 0,008 % und/oder• V: 0,16-0,18 % und/oder• Al: 0,005-0,035 % und/oder• N: 0,008-0,020 %
- Profil nach einem der vorhergehenden Ansprüche, wobei Mn ≥ 1,35 %.
- Profil nach einem der vorhergehenden Ansprüche, wobei die spezifische Wanddicke des Profils höchstens 40 mm ist.
- Profil nach einem der vorhergehenden Ansprüche, wobei die spezifische Wanddicke des Profils höchstens 16 mm ist.
- Profil nach einem der vorhergehenden Ansprüche, wobei das Profil ein geschweißtes Profil oder ein fugenloses Profil ist.
- Verfahren zum Erzeugen eines Hohlprofils aus hochfestem warmgefertigten Stahl nach einem der vorhergehenden Ansprüche, das die folgenden Schritte umfasst:• Gießen einer Stahlplatte, die eine Zusammensetzung gemäß einem der Ansprüche 1 bis 9 aufweist;• (Erneutes) Erhitzen der Stahlplatte auf eine Temperatur von mindestens 1150 °C;• Warmwalzen der Stahlplatte zu einem warmgewalzten Band mit einer Endwalztemperatur im Bereich von 800-950 °C;• Kühlen des warmgewalzten Bandes mit einer Kühlungsrate zwischen 2 und 50 °C/s;• Wickeln des warmgewalzten Bandes bei einer Wickeltemperatur im Bereich von 550-720 °C;• Kaltformen und Schweißen des Bandes, um einen Schlauchrohling zu bilden;• Warmformen des Schlauchrohlings bei Temperaturen im Bereich von 800-1050 °C zu einem endgültigen Hohlprofil mit seinen gültigen Abmessungen;• Kühlen des endgültigen Hohlprofils auf Raumtemperatur;oder das folgende Schritte umfasst:• Herstellen eines Stahlblocks, der eine Zusammensetzung gemäß einem der Ansprüche 1 bis 9 aufweist;• (Erneutes) Erhitzen des Stahlblocks auf eine Temperatur von mindestens 1150 °C;• Durchstechen des heißen Stahlblocks, um eine hohle Rohrschale herzustellen, gefolgt von Walzen der hohlen Rohrschale in einem Stopfenwalzwerk, einem Pilgerwalzwerk oder einem Rohrwalzwerk, um ein Rohr herzustellen;• Wahlweises Durchlaufen des Rohrs durch ein Glättwalzwerk, um die Wanddicke zu reduzieren, und/oder durch eine Größenmessvorrichtung, um den gewünschten Außendurchmesser herzustellen;• Wahlweises erneutes Erhitzen des Rohres auf eine Temperatur im Bereich von 800-950 °C, vorzugsweise durch Induktion, und Rollen in einem Streckreduzierwalzwerk um den Außendurchmesser und/oder die Wanddicke weiter zu reduzieren;• Normalisieren des endgültigen Rohres;• Kühlen des endgültigen Rohres auf Raumtemperatur.
- Verfahren nach Anspruch 13, wobei das Kühlen des endgültigen Hohlprofils auf Raumtemperatur durch Kühlen bei ruhender Luft oder durch Druckluftkühlen erfolgt.
- Verfahren nach einem der Ansprüche 13 oder 14, wobei die Wickeltemperatur des warmgewalzten Bandes mindestens 560 °C und/oder höchstens 650 °C ist.
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NO14823925A NO3084030T3 (de) | 2013-12-18 | 2014-12-11 | |
EP14823925.4A EP3084030B1 (de) | 2013-12-18 | 2014-12-11 | Hohlprofil aus hochfestem warmgefertigtem stahl mit niedrigem kohlenstoffäquivalent für verbessertes schweissen |
PL14823925T PL3084030T3 (pl) | 2013-12-18 | 2014-12-11 | Wysokowytrzymałe, puste w środku, wykańczane na gorąco profile stalowe o niskim ekwiwalencie węgla do ulepszonego spawania |
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EP13198063 | 2013-12-18 | ||
PCT/EP2014/077429 WO2015091216A1 (en) | 2013-12-18 | 2014-12-11 | High strength hot-finished steel hollow sections with low carbon equivalent for improved welding |
EP14823925.4A EP3084030B1 (de) | 2013-12-18 | 2014-12-11 | Hohlprofil aus hochfestem warmgefertigtem stahl mit niedrigem kohlenstoffäquivalent für verbessertes schweissen |
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EP3084030A1 EP3084030A1 (de) | 2016-10-26 |
EP3084030B1 true EP3084030B1 (de) | 2018-02-14 |
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ES (1) | ES2666738T3 (de) |
NO (1) | NO3084030T3 (de) |
PL (1) | PL3084030T3 (de) |
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ES2666738T3 (es) | 2018-05-07 |
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EP3084030A1 (de) | 2016-10-26 |
NO3084030T3 (de) | 2018-07-14 |
WO2015091216A1 (en) | 2015-06-25 |
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