Method for producing a high strength coated steel sheet having improved strength and ductility and obtained sheet

Abstract

A method for producing a high strength coated steel sheet having a yield strength YS of at least 800 MPa, a tensile strength TS of >1180 MPa, a total elongation >14% and a hole expansion ratio HER >30%. The steel contains in weight %: 0.13%≤C≤0.22%, 1.2%≤Si≤1.8%, 1.8%≤Mn≤2.2%, 0.10%≤Mo≤0.20%, Nb≤0.05%, Al≤0.5%, the remainder being Fe and unavoidable impurities. The sheet is annealed at a temperature TA higher than Ac.sub.3 but less than 1000° C. for more than 30 s, then quenched by cooling temperature QT between 325° C. and 375° C., at a cooling speed sufficient to obtain a structure consisting of austenite and at least 60% of martensite, the austenite content being such that the final structure can contain between 3% and 15% of residual austenite and between 85 and 97% of the sum of martensite and bainite, without ferrite, then heated to a partitioning temperature PT between 430° C. and 480° C. and maintained at this temperature for a partitioning time Pt between 10 s and 90 s, then hot dip coated cooled to the room temperature. Coated sheet obtained.

Claims

1. A method for producing a high strength coated steel sheet having an improved strength and an improved formability, the coated steel sheet having a yield strength YS of at least 800 MPa, a tensile strength TS of at least 1180 MPa, a total elongation of at least 14% and a hole expansion ratio HER of at least 30%, comprising the steps of: providing a steel sheet having a chemical composition including in weight %: 0.13%≤C≤0.22%; 1.2%≤Si≤1.8%; 1.8%≤Mn≤2.2%; 0.10%≤Mo≤0.20%; Nb≤0.05%; Al≤0.5%; Ti≤0.05%; and a remainder being Fe and unavoidable impurities; annealing the sheet at an annealing temperature TA higher than Ac.sub.3 but less than 1000° C. for a time of more than 30 s; quenching the sheet by cooling the sheet down to a quenching temperature QT between 325° C. and 375° C. at a cooling speed higher than 30° C./s in order to obtain a structure consisting of austenite and at least 60% of martensite, with an austenite content such that the coated steel sheet has a final structure after coating and cooling to room temperature, including between, by volume fraction, 3% and 15% of residual austenite and between 85% and 97% of a sum of martensite and bainite, the final structure including at least 65% of martensite, the final structure not including ferrite; holding the sheet at the quenching temperature QT for a holding time between 2 s and 8 s; heating the sheet up to a partitioning temperature PT between 430° C. and 480° C. and maintaining the sheet at the partitioning temperature PT for a partitioning time Pt between 10 s and 90 s; hot dip coating the sheet; and cooling the sheet down to room temperature.

2. The method according to claim 1, wherein the quenching temperature QT is between 350° C. and 375° C.

3. The method according to claim 2, wherein the partitioning temperature is between 435° C. and 465° C.

4. The method according to claim 1, wherein the partitioning temperature PT is between 435° C. and 465° C.

5. The method according to claim 1, wherein the chemical composition of the steel satisfies at least one of the following conditions: 0.16%≤C≤0.20%; 1.3%≤Si≤1.6%; and 1.9%≤Mn≤2.1%.

6. The method according to claim 1, wherein the hot dip coating is a galvanizing step.

7. The method according to claim 1, wherein the hot dip coating step is a galvannealing step with an alloying temperature TGA between 480° C. and 510° C.

8. The method according to claim 7, wherein the partitioning time Pt is between 50 s and 70 s.

9. The method according to claim 1, wherein the holding time at the quenching temperature is between 3 s and 7 s.

10. The method according to claim 1, wherein the partitioning time is between 10 s and 30 s.

Description

(1) The invention will now be described in details but without introducing limitations and illustrated by the FIGURE which is a micrograph of an example of the invention.

(2) According to the invention, the sheet is obtained by hot rolling and optionally cold rolling of a semi product which chemical composition contains, in weight %: 0.13% to 0.22%, and preferably more than 0.16% preferably less than 0.20% of carbon for ensuring a satisfactory strength and improving the stability of the retained austenite which is necessary to obtain a sufficient elongation. If carbon content is too high, the hot rolled sheet is too hard to cold roll and the weldability is insufficient. 1.2% to 1.8%, preferably more than 1.3% and less than 1.6% of silicon in order to stabilize the austenite, to provide a solid solution strengthening and to delay the formation of carbides during overaging without formation of silicon oxides at the surface of the sheet which is detrimental to coatability. 1.8% to 2.2% and preferably more than 1.9% and preferably less than 2.1% of manganese to have a sufficient hardenability in order to obtain a structure containing at least 65% of martensite, tensile strength of more than 1150 MPa and to avoid having segregation issues which are detrimental for the ductility. 0.10% to 0.20% of molybdenium to increase the hardenability and to stabilize the retained austenitic in order to strongly reduce austenite decomposition during overaging. up to 0.5% of aluminium which is usually added to liquid steel for the purpose of deoxidation, preferably, the Al content is limited to 0.05%. If the content of Al is above 0.5%, the austenitizing temperature will be too high to be easily reached and the steel will become industrially difficult to process. Nb content and Ti content are limited to 0.05% each because above such values numerous precipitates will form and formability will decrease, making the 14% of total elongation more difficult to reach.

(3) The remainder being iron and residual elements resulting from the steelmaking. In this respect, Ni, Cr, Cu, V, B, S, P and N at least are considered as residual elements which are unavoidable impurities. Therefore, generally, their contents are less than 0.05% for Ni, 0.10% for Cr, 0.03 for Cu, 0.007% for V, 0.0010% for B, 0.005% for S, 0.02% for P and 0.010% for N.

(4) The sheet is prepared by hot rolling and optionally cold rolling according to the methods known by those who are skilled in the art.

(5) After rolling the sheets are pickled or cleaned then heat treated and hot dip coated.

(6) The heat treatment which is made preferably on a combined continuous annealing and hot dip coating line comprises the steps of: annealing the sheet at an annealing temperature TA higher than the Ac.sub.3 transformation point of the steel, and preferably higher than Ac.sub.3+15° C., in order to be sure that the structure is completely austenitic, but less than 1000° C. in order not to coarsen too much the austenitic grains. Generally, a temperature higher than 865° C. is enough for the steel according to the invention. The sheet is maintained at the annealing temperature i.e. maintained between TA−5° C. and TA+10° C., for a time sufficient to homogenize the chemical composition. Preferably, the time is of more than 30 s but does not need to be of more than 300 s. quenching the sheet by cooling down to a quenching temperature QT lower than the Ms transformation point at a cooling rate enough to avoid ferrite and bainite formation. The quenching temperature is between 325° C. and 375° C. and preferably between 350° C. and 375° C. in order to have, just after quenching, a structure consisting of austenite and at least 60% of martensite, the austenite content being such that the final structure i.e. after treatment, coating and cooling to the room temperature, can contain between 3% and 15% of residual austenite and between 85 and 97% of the sum of martensite and bainite, without ferrite. A cooling rate higher than 30° C./s is enough, reheating the sheet up to a partitioning temperature PT between 430° C. and 480° C. and preferably between 435° C. and 465° C. For example, the partitioning temperature can be equal to the temperature at which the sheet must be heated in order to be hot dip coated, i.e. between 455° C. and 465° C. The reheating rate can be high when the reheating is made by induction heater, but that reheating rate had no apparent effect on the final properties of the sheet. Preferably, between the quenching step and the step of reheating the sheet to the partitioning temperature PT, the sheet is held at the quenching temperature for a holding time comprised between 2 s and 8 s, preferably between 3 s and 7 s. maintaining the sheet at the partitioning temperature PT for a partitioning time Pt between 10 s and 90 s. Maintaining the sheet at the partitioning temperature means that during partitioning the temperature of the sheet remains between PT−20° C. and PT+20° C. optionally, adjusting the temperature of the sheet by cooling or heating in order to be equal to the temperature at which the sheet has to be heated in order to be hot dip coated. hot dip coating the sheet, the hot dip coating being, for example, galvanizing or galvannealing, but all type of metallic hot dip coating is possible provided that the temperatures at which the sheet is brought to during coating remains less than 650° C. When the sheet is galvanized, it is done with the usual conditions. When the sheet is galvannealed, the temperature of alloying TGA must not be too high to obtain good final mechanical properties. This temperature is preferably between 480° C. and 510° C. Moreover, in this case, the partitioning time is preferably between 50 s and 70 s. generally, after coating, the sheet is processed according to the known art. In particular the sheet is cooled to the room temperature.

(7) With such treatment, coated sheets having a yield strength YS of at least 800 MPa, a tensile strength of at least 1180 MPa, a total elongation of at least 14% and a hole expansion ratio HER according to the ISO standard 16630:2009 of at least 30% can be obtained.

(8) As an example a sheet of 1.2 mm in thickness having the following composition: C=0.18%, Si=1.5% Mn=2.0%, Nb=0.02%, Mo=0.15%, the remainder being Fe and impurities, was manufactured by hot and cold rolling. The theoretical Ms transformation point of this steel is 386° C. and the Ac.sub.3 point is 849° C.

(9) Samples of the sheet were heat treated by annealing, quenching and partitioning then galvanized or galvannealed, and the mechanical properties were measured.

(10) The conditions of treatment and the obtained properties are reported at table I for the samples that were galvanized and at table II for the samples that were galvannealed.

(11) TABLE-US-00001 TABLE I TA QT PT Pt YS TS UE TE HER Sample ° C. ° C. ° C. s MPa MPa % % % 1 900 300 460 60 1116 1207 7 12 2 900 350 460 30 952 1215 9 14 3 900 350 460 60 926 1199 8 14 31 4 900 350 460 90 909 1207 9 14 5 900 400 460 60 709 1187 10 15 6 900 460 460 60 685 1178 9 14

(12) TABLE-US-00002 TABLE II TA QT PT Pt TGA YS TS UE TE HER Sample ° C. ° C. ° C. s ° C. MPa MPa % % % 7 900 350 460 60 500 838 1185 9 14 34 8 900 350 460 60 520 854 1215 9 12 9 900 350 460 60 520 869 1167 8 12 -20 s- 10 900 350 460 60 570 898 1106 7 13

(13) In these tables, TA is the annealing temperature, QT the quenching temperature, PT the partitioning temperature, Pt the maintaining time at the partitioning temperature, TGA the temperature of alloying for the sheets that were galvannealed, YS the yield strength, TS the tensile strength, UE the uniform elongation, TE the total elongation and HER the hole expansion ratio measured according to the ISO 16630:2009 standard.

(14) For example 9, “520-20” (TGA) means that the steel has been at the GA temperature of 520° C. for 20 seconds, in the other examples (7, 8 and 10) once the GA temperature is reached, then the temperature decreases slowly before the final cooling.

(15) Examples 1 to 4 show that with a quenching temperature equal or less than 350° C., a partitioning at a temperature of 460° C. with a partitioning time from 30 s to 90 s galvanized sheets have a yield strength higher than 800 MPa, a tensile strength higher than 1180 MPa, a total elongation of more than or equal to 12% and a hole expansion ratio measured according to ISO standard 16630: 2009 higher than 30%.

(16) Examples for which the quenching temperature is higher than Ms are comparative examples and/or according to the prior art. The structure contains ferrite or bainite and austenite and the yield strength is significantly less than 800 MPa.

(17) The examples 7 to 10 show that, when the sheet is galvannealed, the temperature of alloying has to be as low as possible to obtain a total elongation of 14% and a hole expansion ratio HER of more than 30%. Example 7, a micrograph of which is shown at the FIGURE, contains 4% of retained austenite and 96% of the sum of martensite and bainite.

(18) The conditions of treatment and the obtained properties are reported at table I for the samples that were galvanized and at table II for the samples that were galvannealed.