EP1682686B1 - Für das galvanisieren geeignetes zweiphasenstahlband - Google Patents
Für das galvanisieren geeignetes zweiphasenstahlband Download PDFInfo
- Publication number
- EP1682686B1 EP1682686B1 EP04752656.1A EP04752656A EP1682686B1 EP 1682686 B1 EP1682686 B1 EP 1682686B1 EP 04752656 A EP04752656 A EP 04752656A EP 1682686 B1 EP1682686 B1 EP 1682686B1
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- European Patent Office
- Prior art keywords
- strip
- temperature
- steel
- soak
- max
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- 238000005246 galvanizing Methods 0.000 title claims description 17
- 229910000885 Dual-phase steel Inorganic materials 0.000 title description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 52
- 239000010959 steel Substances 0.000 claims description 52
- 229910000734 martensite Inorganic materials 0.000 claims description 27
- 238000001816 cooling Methods 0.000 claims description 19
- 239000011572 manganese Substances 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 16
- 239000011651 chromium Substances 0.000 claims description 15
- 229910052799 carbon Inorganic materials 0.000 claims description 12
- 238000002791 soaking Methods 0.000 claims description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 11
- 229910000859 α-Fe Inorganic materials 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 6
- 239000011733 molybdenum Substances 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 239000008397 galvanized steel Substances 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 239000011593 sulfur Substances 0.000 claims description 4
- 239000010936 titanium Substances 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 238000005244 galvannealing Methods 0.000 claims description 3
- 239000004615 ingredient Substances 0.000 claims description 3
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims 2
- 229910052698 phosphorus Inorganic materials 0.000 claims 2
- 239000011574 phosphorus Substances 0.000 claims 2
- 239000000203 mixture Substances 0.000 description 17
- 230000009977 dual effect Effects 0.000 description 11
- 238000000137 annealing Methods 0.000 description 9
- 229910001563 bainite Inorganic materials 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 7
- 230000015572 biosynthetic process Effects 0.000 description 6
- 239000011248 coating agent Substances 0.000 description 5
- 238000000576 coating method Methods 0.000 description 5
- 239000010960 cold rolled steel Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- 229910000655 Killed steel Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 101100328895 Caenorhabditis elegans rol-8 gene Proteins 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- XTKDAFGWCDAMPY-UHFFFAOYSA-N azaperone Chemical compound C1=CC(F)=CC=C1C(=O)CCCN1CCN(C=2N=CC=CC=2)CC1 XTKDAFGWCDAMPY-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000005088 metallography Methods 0.000 description 1
- 230000000153 supplemental effect Effects 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
Definitions
- Dual phase galvanized steel strip is made utilizing a thermal profile involving a two-tiered isothermal soaking and holding sequence.
- the strip is at a temperature close to that of the molten metal when it enters the coating bath.
- a cold rolled steel sheet is used as the base for hot dip galvanizing, the steel sheet having a particular composition which is said to be beneficial for the formation, under the conditions of the process, of a microstructure composed mainly of ferrite and martensite.
- the Omiya et al patent describes a galvanized dual phase product.
- a dual phase galvanized steel sheet is made by soaking the cold rolled steel sheet at a temperature of 780°C (1436°F) or above, typically for 10 to 40 seconds, and then cooling it at a rate of at least 5°C per second, more commonly 20-40°C per second, before entering the galvanizing bath, which is at a temperature of 460°C (860°F).
- the steel should have a composition as follows, in weight percent: Carbon: 0.02-0.20 Aluminum: 0.010-0.150 Titanium: 0.01 max Silicon: 0.04 max Phosphorous: 0.060 max Sulfur: 0.030 max Manganese: 1.5-2.40 Chromium: 0.03-1.50 Molybdenum:0.03-1.50 with the provisos that the amounts of manganese, chromium and molybdenum should have the relationship: 3Mn + 6Cr + Mo: 8.1% max, and Mn + 6Cr + 10 Mo: at least 3.5%
- the plated sheet After plating, cooling at a rate of at least 5°C/second will achieve the desired microstructure of predominantly ferrite and martensite.
- the plated sheet may be heated prior to cooling, in an alloying procedure (often called galvannealing) after metal coating but prior to the final cooling.
- the soak temperature of (A C 1 +45°F) to 1425°F, usually 1340-1420°F must be coupled with a subsequent substantially isothermal heat treatment, termed the holding step, in the range of 850-920°F (454-493°C).
- the holding step the sheet is maintained at 850-920°F (454-493°C), sometimes herein expressed as 885°F ⁇ 35°F, for a period of 20 to 100 seconds, before cooling to room (ambient) temperature.
- Cooling to ambient temperature should be conducted at a rate of at least 5°C per second. It is important to note, once again, that the Omiya et al patent says nothing about a holding step at any temperature or for any time in their thermal process. Furthermore, my work has shown that if a steel as defined in the Omiya et al patent is soaked within Omiya's defined, higher, soaking range (for example 1475°F) and further processed through a thermal cycle including a holding step as described herein (850-920F), the resultant steel will not achieve the desired predominantly ferrite-martensite microstructure but will contain a significant amount of bainite and/or pearlite.
- the steel sheet should have a composition similar to that of the Omiya et al patent: Carbon: 0.02-0.20 Aluminum: 0.010-0.150 Titanium: 0.01 max Silicon: 0.04 max Phosphorous: 0.060 max Sulfur: 0.030 max Manganese: 1.5-2.40 Chromium: 0.03-1.50 Molybdenum:0.03-1.50 with the provisos that the amounts of manganese, chromium and molybdenum could have the relationship: Mn + 6Cr + 10 Mo: at least 3.5%
- the silicon content may be as much as 0.5%, and, preferably, carbon content is 0.03-0.12% although the Omiya et al carbon range may also be used.
- This composition, as modified, may be referred to hereafter as Composition A.
- my invention is a method of making a dual phase steel sheet comprising soaking a steel sheet at a temperature of in the range from A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), for a period of 20 to 90 seconds, cooling the sheet at a rate no lower than 1°C/second to a temperature of 454-493°C, and holding the sheet at temperatures in the range of 850-920°F (454-493°C) for a period of 20 to 100 seconds.
- the holding step may be prior to the hot dip or may begin with the hot dip, as the galvanizing pot will be at a temperature also in the range 454-493°C (850-920°F).
- the sheet can be cooled to ambient temperature at a rate of at least 5°C/second.
- the sheet may be galvannealed in the conventional manner - that is, the sheet is heated for about 5-20 seconds to a temperature usually no higher than about 960°F and then cooled at a rate of at least 5°C/second.
- My galvannealed and galvanized thermal cycles are shown for comparison in Figure 6 .
- the actual hot dip step is conducted more or less conventionally - that is, the steel is contacted with the molten galvanizing metal for about 5 seconds; while a shorter time may suffice in some cases, a considerably longer time may be used but may not be expected to result in an improved result.
- the steel strip is generally about 0.7 mm thick to about 2.5 mm thick, and the coating will typically be about 10 ⁇ m.
- the coated steel may be either cooled to ambient temperature as described elsewhere herein or conventionally galvannealed, as described above. When the above protocol is followed, a product having a microstructure comprising mainly ferrite and martensite will be obtained.
- my invention comprises feeding a cold rolled coil of steel strip of Composition A to a heating zone in the galvanizing line, passing the strip through a heating zone continuously to heat the strip to within the range of A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), passing the strip through a soaking zone to maintain the strip within the range of A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), for a period of 20 to 90 seconds, passing the strip through a cooling zone to cool the strip at a rate greater than 1°C/second, discontinuing cooling the strip when the temperature of the strip has been reduced to a temperature in the range 885°F ⁇ 35°F, but also ⁇ 30 degrees F of the temperature of the
- the galvanizing bath is typically at about 870°F (850-920°F), and may be located at the beginning of the holding zone, or near the end of the hold zone, or anywhere else in the holding zone, or immediately after it. Residence time in the bath is normally 3-6 seconds, but may vary somewhat, particularly on the high side, perhaps up to 10 seconds. As indicated above, after the steel is dipped into and removed from the zinc bath, the sheet can be heated in the conventional way prior to cooling to room temperature to form a galvanneal coating, if desired.
- Samples of steel sheet were processed, with various "soak" temperatures according to the general thermal cycle depicted in Figure 1 - one set of samples followed the illustrated curve with a 35 second "hold” at 880°F and the other set of samples were held at 880°F for 70 seconds.
- the samples were cold rolled steel of composition A as described above - in particular, the carbon was 0.67, Mn was 1.81, Cr was 0.18 and Mo was 0.19, all in weight percent.
- the other elemental ingredients were typical of low carbon, A1 killed steel. Soak temperatures were varied in increments of 20°F within the range of 1330 to 1510°F. After cooling, the mechanical properties and microstructures of the modified samples were determined.
- UTS Ultimate tensile strength
- a goal of Example 1 was to achieve a predominantly ferrite-martensite microstructure.
- the yield ratio i.e. the ratio of yield strength to ultimate tensile strength, is an indication whether or not a dual phase ferrite-martensite microstructure is present.
- a ferrite-martensite microstructure is indicated when the yield ratio is 0.5 or less. If the yield ratio is greater than about 0.5, a significant volume fraction of other deleterious constituents such as bainite, pearlite, and/or Fe 3 C may be expected in the microstructure.
- Figure 3 shows the yield ratio as a function of soak temperature for both the 35 and 70 second holding zones for the samples.
- the necessary annealing range for ferrite-martensite microstructures is from about 1350 to 1430°F.
- Table 1 summarizes the relationships between the thermal process, yield ratio and microstructural constituents for this example at the different soak temperature regimes.
- a different cold rolled sheet steel of Composition A was subjected to the same set of thermal cycles a described in Example 1 and shown in Figure 1 .
- This steel also lay within the stated composition range, in this case specifically containing the following, in weight percent: 0.12%C, 1.96%Mn, 0.24%Cr, and 0.18%Mo, and the balance of the composition typical for a low carbon Al-killed steel.
- the effect of soak temperature on yield ratio for this steel for the 70 second holding sequence at 880°F is shown in Figure 4 .
- This curve exhibits a shape similar to the curves in Figure 3 , with metallographic analyses revealing identical metallogical phenomena occurring at the different soak temperature regimes as in the previous example.
- the annealing soak temperature range necessary for a predominantly ferrite-martensite microstructure to be obtained is from about 1350 to 1425°F when a hold step is conducted at about 880°F.
- a third cold-rolled steel of Composition A was processed according to the set of thermal cycles shown in Figure 1 .
- This steel contained, in weight percent, 0.076C, 1.89 Mn, 0.10Cr, 0.094 Mo, and 0.34 Si, the balance of which is typical for a low carbon steel.
- Figure 5 shows the yield ratio of this material as a function of soak temperature for the holding time of 70 seconds.
- the soak temperature range necessary for dual phase production depends on the specific steel composition - that is, it should lie within the range from A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C) when a holding step in the vicinity of 880° (885°F ⁇ 35°F) is present in the thermal cycle.
- Table 3 shows the resultant mechanical properties of two additional steels having carbon contents lower than shown previously. They were processed as described in Figure 1 utilizing the individual soak temperatures of 1365, 1400, and 1475°F, respectively and a hold time of 70 seconds at 880°F. Also shown within the table are the expected necessary soak temperature ranges for dual phase steel production for each steel as calculated from A c1 as described in Example 3. Note that for the 1365 and 1400°F soak temperatures, which reside within the desired soak temperature range for both respective steels, low yield ratios characteristic of ferrite-martensite microstructures are observed. Furthermore, for the steels soaked at 1475°F, which is outside the range present invention, the yield ratio is significantly higher due to the presence of bainite in the microstructure.
- Table 3a displays data collected in a manner similar to that of Table 3: Table 3a C Mn Mo Cr Ac1 A C1 +45 -A C1 +135 Soak° F YS UTS YS/U TS .058 1.23 0.4 0.2 1316 1361 - 1451 1400 251 524 0.48 .058 1.23 0.4 0.2 1316 1361 - 1451 1500 304 520 0.58 .121 1.22 0.4 0.2 1316 1361 - 1451 1400 291 619 0.47 .121 1.22 0.4 0.2 1316 1361 - 1451 1500 328 614 0.53
- my invention includes the use of a soak temperature in the range of A C1 +45°F to A C1 +135°F for the defined compositions, without caps.
- steels 1 through 4 were soaked within the soaking range of the invention and exhibited the expected yield ratio of less than 0.5.
- Metallographic examination revealed the presence of ferrite martensite microstructures for steels 1 through 4 with martensite contents of about 15%.
- Steel 5 was processed outside of the preferred soaking range and exhibited a relatively high yield ratio of about 0.61.
- Metallographic analysis showed a bainite content of 11% in this material. Similar results have been shown for galvanize as well as galvanneal processing.
- the hold temperature may be within the range of 850-940°F (that is, 895°F ⁇ 45°F), and need not be limited to 850-920°F as previously stated.
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Claims (4)
- Verfahren zum Herstellen eines galvanisierten Stahlbandes, das vorherrschend ein Martensit- und Ferrit-Mikrogefüge hat, wobei der Stahl folgende Bestandteile in Gewichtsprozent hat: Kohlenstoff: 0,02-0,20; Aluminium: 0,010-0,150; Titan: max. 0,01; Silizium: max. 0,5; Phosphor: max 0,060; Schwefel: max 0,030; Mangan: 0,8-2,40; Chrom: 0,03-1,50; Molybdän: 0,03-1,50, umfassend das Durchwärmen des Stahlbandes bei einer Temperatur im Bereich von 727°C (1.340°F) bis 775°C (1.425°F) für wenigstens 20 Sekunden, das Kühlen des Bandes mit einer Rate von wenigstens 1°C pro Sekunde, das Leiten des Bandes durch einen Galvanisierkessel für eine Verbleibszeit von 2 bis 9 Sekunden darin, um das Band zu beliebiger Zeit zu beschichten, während das Band auf einer Temperatur zwischen 455°C und 505°C (895°F ± 45°F) für 20 bis 100 Sekunden gehalten wird, und das Kühlen des auf diese Weise beschichteten Bandes auf Umgebungstemperatur;
mit der Maßgabe, dass ein Verfahren zum Herstellen eines galvanisierten Stahlbandes, das vorherrschend ein Martensit- und Ferrit-Mikrogefüge hat, ausgeschlossen ist, bei dem der Stahl folgende Bestandteile in Gewichtsprozent hat: Kohlenstoff: 0,02-0,20; Aluminium: 0,010-0,150; Titan: max. 0,01; Silizium: max. 0,5; Phosphor: max 0,060; Schwefel: max 0,030; Mangan: 1,5-2,40; Chrom: 0,03-1,50; Molybdän: 0,03-1,50, umfassend das Durchwärmen des Stahlbandes bei AC1+45°F, jedoch wenigstens 727°C (1.340°F), bis AC1+135°F, jedoch nicht mehr als 775°C (1.425°F) für wenigstens 20 Sekunden, das Kühlen des Bandes mit einer Rate von wenigstens 1°C pro Sekunde, das Leiten des Bandes durch einen Galvanisierkessel für eine Verbleibszeit von 2 bis 9 Sekunden darin, um das Band zu beliebiger Zeit zu beschichten, während das Band auf einer Temperatur zwischen 455°C und 494°C (885°F ± 35°F) für 20 bis 100 Sekunden gehalten wird, und das Kühlen des auf diese Weise beschichteten Bandes auf Umgebungstemperatur. - Verfahren nach Anspruch 1, umfassend das Wärmegalvanisieren des Bandes vor dem Kühlen auf Umgebungstemperatur.
- Verfahren nach Anspruch 1, bei dem sich das Band innerhalb 30°F der Temperatur des Galvanisierkessels während der Verbleibszeit darin befindet.
- Verfahren nach Anspruch 1, bei dem sich das Band innerhalb 20°F der Temperatur des Galvanisierkessels während der Verbleibszeit darin befindet.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
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PL04752656T PL1682686T3 (pl) | 2003-11-04 | 2004-05-17 | Taśma z dwufazowej stali odpowiednia do galwanizacji |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/US2003/035095 WO2004048634A1 (en) | 2002-11-26 | 2003-11-04 | Method for the production of dual phase sheet steel |
PCT/US2004/015675 WO2005047550A1 (en) | 2003-11-04 | 2004-05-17 | Dual phase steel strip suitable for galvanizing |
Publications (3)
Publication Number | Publication Date |
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EP1682686A1 EP1682686A1 (de) | 2006-07-26 |
EP1682686A4 EP1682686A4 (de) | 2007-06-27 |
EP1682686B1 true EP1682686B1 (de) | 2014-11-12 |
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EP04752656.1A Expired - Lifetime EP1682686B1 (de) | 2003-11-04 | 2004-05-17 | Für das galvanisieren geeignetes zweiphasenstahlband |
Country Status (6)
Country | Link |
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EP (1) | EP1682686B1 (de) |
AU (1) | AU2004289949B2 (de) |
CA (1) | CA2544382C (de) |
ES (1) | ES2530066T3 (de) |
PL (2) | PL210446B3 (de) |
WO (1) | WO2005047550A1 (de) |
Families Citing this family (1)
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JP5223360B2 (ja) * | 2007-03-22 | 2013-06-26 | Jfeスチール株式会社 | 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
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EP0048761B1 (de) * | 1980-03-31 | 1984-07-04 | Kawasaki Steel Corporation | Hochfestes, kaltgewalztes stahlblech sowie hochfestes, verzinktes stahlblech mit jeweils ausgezeichneter verformbarkeit und verfahren zur herstellung derselben |
AU744962B2 (en) * | 1999-02-22 | 2002-03-07 | Nippon Steel & Sumitomo Metal Corporation | High strength galvanized steel plate excellent in adhesion of plated metal and formability in press working and high strength alloy galvanized steel plate and method for production thereof |
US6312536B1 (en) * | 1999-05-28 | 2001-11-06 | Kabushiki Kaisha Kobe Seiko Sho | Hot-dip galvanized steel sheet and production thereof |
EP1227167B1 (de) * | 2000-01-24 | 2006-01-18 | JFE Steel Corporation | Feuerverzinktes stahlblech und herstellungsverfahren dafür |
TW520398B (en) * | 2000-11-28 | 2003-02-11 | Kawasaki Steel Co | Composite structure type high tensile strength steel plate, plated plate of composite structure type high tensile strength steel and method for their production |
US6586117B2 (en) * | 2001-10-19 | 2003-07-01 | Sumitomo Metal Industries, Ltd. | Steel sheet having excellent workability and shape accuracy and a method for its manufacture |
US6811624B2 (en) * | 2002-11-26 | 2004-11-02 | United States Steel Corporation | Method for production of dual phase sheet steel |
-
2004
- 2004-05-17 PL PL379761A patent/PL210446B3/pl unknown
- 2004-05-17 AU AU2004289949A patent/AU2004289949B2/en not_active Ceased
- 2004-05-17 EP EP04752656.1A patent/EP1682686B1/de not_active Expired - Lifetime
- 2004-05-17 ES ES04752656.1T patent/ES2530066T3/es not_active Expired - Lifetime
- 2004-05-17 CA CA2544382A patent/CA2544382C/en not_active Expired - Fee Related
- 2004-05-17 WO PCT/US2004/015675 patent/WO2005047550A1/en active Application Filing
- 2004-05-17 PL PL04752656T patent/PL1682686T3/pl unknown
Also Published As
Publication number | Publication date |
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AU2004289949B2 (en) | 2011-04-28 |
ES2530066T3 (es) | 2015-02-26 |
AU2004289949A1 (en) | 2005-05-26 |
EP1682686A1 (de) | 2006-07-26 |
WO2005047550A1 (en) | 2005-05-26 |
PL379761A1 (pl) | 2006-11-13 |
PL210446B3 (pl) | 2012-01-31 |
PL1682686T3 (pl) | 2015-04-30 |
EP1682686A4 (de) | 2007-06-27 |
CA2544382A1 (en) | 2005-05-26 |
CA2544382C (en) | 2010-04-06 |
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