Classifications

• • 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
  • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
  • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
  • C21D8/1222—Hot rolling
• • 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
• • 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
  • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
  • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
  • C21D8/1233—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—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

Definitions

• the invention relates to a process for producing a cold-rolled or hot-rolled steel strip of a relatively high strength dual phase steel with excellent forming properties, in particular for lightweight vehicle construction according to the preamble of claim 1 .
• a crucial role plays hereby weight saving of all vehicle components, on the one hand, but also a beneficial behavior of the individual components when exposed to high static and dynamic stress during operation and in the event of a crash, on the other hand.
• Suppliers attempt to take this requirement into account in such a way that the wall thickness can be reduced through use of high strength and super high strength steels while at the same time improving the component behavior during its manufacture thereof and at operation.
• Such steels have to meet therefore comparably high standards with respect to strength, stretching capacity, toughness, energy consumption and workability, for example by cold forming, welding and/or surface treatment.
• Dual phase steels find increasingly application in this area as a result of their excellent formability and high strength values at the same time.
• Dual phase steels have hereby mainly ferritic-martensitic structure.
• cold-rolled steel strips are normally subjected to recrystallization annealing by way of a continuous annealing process into a metal sheet that is easy to shape.
• furnace parameters run-through speed, annealing temperature, rate of cooling
• the furnace parameters are adjusted in dependence on the alloy composition and strip thickness in accordance with the demanded microstructure and mechanical-technological properties.
• the dual phase microstructure is adjusted by heating the cold bath in the continuous annealing furnace to such a temperature that the required ferritic-martensitic microstructure is formed during cooling.
• the annealing treatment is normally carried out in a continuous annealing furnace upstream of the galvanizing bath.
• the required dual phase microstructure is occasionally adjusted depending on the alloying concept only during annealing treatment in the continuous furnace in order to be able to realize the demanded mechanical properties on the basis of an austenitic microstructure which is as homogenous as possible.
• the known steels In order for the steels to attain a transformation inertia that is sufficient for realizing the demanded dual phase microstructure, when the cold strip undergoes recrystallizing annealing, the known steels have respective contents, e.g. of Cr, Mo, Nb, or B. In particular the costly elements Cr and Mo have an adverse impact on the manufacturing costs of the dual phase steel.
• a narrow process window is to be understood in this context as a need to adjust the run-through speed in dependence on thickness of the strip to be annealed in order to attain a homogenous temperature distribution in the strip and the demanded dual phase microstructure and the mechanical-technological properties during cooling.
• the demanded strip properties can be realized even when the strips to be annealed have different thickness while the furnace parameters remain the same.
• a homogenous temperature distribution is difficult to realize in particular in the transition zone from one strip to another, when different thicknesses are involved, and lead in the event of alloy compositions with too small process window to a situation in which the advance of the thinner strip through the furnace is too slow, causing a lower productivity, or the advance of the thicker strip through the annealing furnace is too fast, posing the risk of failure to realize a homogenous temperature distribution and thus the demanded mechanical-technological properties. As a result, increasing waste and even customer complaints are encountered.
• the regions of smaller sheet thickness in flexibly rolled hot or cold strips of steel of known compositions have strengths that are too low as a result of the substantial proportion of ferrite in view of the transformation processes during cooling, or the regions of greater sheet thickness reach values that are too high as a result of the substantial proportion of martensite.
• Homogenous mechanical-technological properties over the strip length or across the strip width are virtually impossible to attain, when using the known alloying concepts during continuous annealing.
• the invention is therefore based on the object to provide a different more cost-efficient alloying concept for a relatively high-strength steel with dual phase microstructure that allows a broadening of the process window for continuous annealing of hot or cold strips in such a way that in addition to strips of varying thickness also steel strips of varying thickness over the strip length and, optionally, across the strip width can be produced having mechanical-technological properties which are as homogenous as possible.
• Nb 0 . 01
• V 0 . 02
• the demanded dual phase microstructure is produced during continuous annealing, and wherein the cold-rolled or hot-rolled steel strip is heated in the continuous annealing furnace in a one-step process to a temperature in the range of 820 to 1000° C., preferably 840 to 1000° C., and the annealed steel strip is then cooled down from the annealing temperature with a rate of cooling between 15 and 30° C./s.
• the relatively high strength dual phase steel in accordance with the invention for the lightweight vehicle construction is characterized in that the targeted addition of V and Nb while omitting the cost-intensive alloying elements Mo or CR results in a transformation inertia which is high enough to enable with very high process reliability an adjustment of the demanded dual phase microstructure with homogenous mechanical-technological properties during continuous annealing from a completely austenitic matrix even when strips are involved having a thickness which varies over the strip length or across the strip width.
• the steel according to the invention offers the benefit of a significantly greater process window compared to known steels.
• process reliability is enhanced during continuous annealing or hot dip galvanizing of cold and hot strips with dual phase microstructure.
• homogenous mechanical-technological properties in the strip can be assured in hot-galvanized as well as continuously annealed hot or cold strips. This applies for continuous annealing of successive strips with different strip thickness and in particular for strips with varying sheet thickness over the strip length and/or strip width.
• load-optimized components can be advantageously manufactured from this material through shaping.
• a dual phase steel is involved having approx. 20% martensite embedded in the form of islands in the strength class of about 800 MPa. in particular for hot dip galvanizing as well as for the application in a continuous annealing facility.
• the fine-grained configuration of the microstructure and the mechanical-technological properties can be adjusted in accordance with the invention via the formation of nitrides or carbonitrides in dependence on the N-content of the steel.
• Nb and in particular V which cause a transformation-inert or transformation-free zone during cooling.
• the steel has in accordance with the invention a V content of at least 0.02% and a Nb content of at least 0.01%.
• Nb acts hereby as grain refining element, with the extent of the Nb addition being suited to the actual C and N contents of the steel.
• V is also adjusted in accordance with the invention to the contents of C and N, with the extent of the addition being suited however in such a way that enough V is kept in solution in order to realize a sufficient transformation inertia.
• the V content amounts to at least 0.06 to 0.10% and the Nb content to more than 0.02 to 0.05%. Further increase of the contents of V and Nb does not provide any further benefits as far as a further retarded transformation of the steel is concerned and thus for the broadness of the process window during continuous annealing.
• the annealed strip is first heated to a temperature that causes a completely austenitic microstructure.
• the annealing temperatures range hereby for the steel according to the invention between approx. 820 and approx. 1000° C., depending on the concrete alloy composition.
• the adjusted content of ferrite and (residue) austenite during cooling is maintained until after the process step “galvanizing”.
• the still present proportion of austenite is then fully transformed into martensite during continued cooling.
• the galvanizing parameters may vary over a wide range.
• the galvanizing speeds range between 60 and 120 m/min depending on the sheet thickness.
• the rate of cooling before and after the galvanizing bath ranges at fairly low 10 to 30° C./sec.
• the produced material may be processed as cold bath as well as also hot bath, in dressed and undressed but also heat-treated state (intermediate annealing) via a hot dip galvanizing line or a pure continuous annealing facility.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Electromagnetism (AREA)
• Manufacturing & Machinery (AREA)
• Heat Treatment Of Sheet Steel (AREA)

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• 2006
  • 2006-11-14 DE DE102006054300A patent/DE102006054300A1/de not_active Ceased
• 2007
  • 2007-11-13 KR KR1020097009714A patent/KR20090089311A/ko not_active Application Discontinuation
  • 2007-11-13 WO PCT/DE2007/002074 patent/WO2008058530A1/de active Application Filing
  • 2007-11-13 US US12/514,716 patent/US20100000634A1/en not_active Abandoned
  • 2007-11-13 EP EP07817796.1A patent/EP2094876B1/de active Active
  • 2007-11-13 RU RU2009122381/02A patent/RU2443787C2/ru active

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