EP1563105A1

EP1563105A1 - Method for making an abrasion resistant steel plate and plate obtained

Info

Publication number: EP1563105A1
Application number: EP03786006A
Authority: EP
Inventors: Jean Beguinot; Jean-Georges Brisson
Original assignee: Industeel Creusot
Current assignee: Industeel Creusot
Priority date: 2002-11-19
Filing date: 2003-11-13
Publication date: 2005-08-17
Anticipated expiration: 2023-11-13
Also published as: ATE382716T1; AU2003295014B2; FR2847272B1; AU2003295014A1; KR101010571B1; FR2847272A1; WO2004048619A1; BR0315693B1; PL202086B1; CN1714159A; DE60318478T2; PL375543A1; KR20050083903A; RU2005119205A; BR0315693A; US20060162826A1; CA2506349C; JP2006506527A; UA78624C2; DE60318478D1

Abstract

The invention concerns a method for making an abrasion resistant steel plate having a chemical composition comprising, by weight: 0.24 % ≤ C ≤ 0.35 %; 0 % ≤ Si ≤ 2 %; 0 % ≤ AI ≤ 2 %; 0.5 % ≤ Si + AI ≤ 2 %; 0 % ≤ Mn ≤ 2.5 %; 0 % ≤ Ni ≤ 5 %; 0 % ≤ Cr ≤< 5 %; 0 % ≤ Mo ≤ 1 %; 0 % ≤W ≤ 2 %; 0.1 % ≤ Mo +W/2 ≤ 1 %; 0 % ≤ B ≤ 0.02 %; 0 % ≤ Ti ≤ 1.1 %; 0 % ≤ Zr ≤ 2.2 %; 0.35 % ≤ Ti + Zr/2 ≤ 1.1 %; 0 % ≤ S < 0,15 %; N <0,03 %, optionally 0 % to 1,5 % of copper; optionally at least one element selected among Nb, Ta and V in contents such that Nb/2 + Ta/4 + V ≤ 0.5 %; optionally at least one element selected among Te, Ca, Bi, Pb in contents not more than 0.1 %; the rest being iron and impurities resulting from the preparation, moreover the chemical composition satisfying the following relationships: 0.095 % ≤ C* = C - Ti/4 - Zr/8 + 7xN/8 and 1.05xMn + 0,54xNi +0.50xCr + 0.3x(Mo + W/2)112 + K > 1.8, with K = 0.5 if B ≤ 0.0005 % and K = 0 if B < 0.0005 %. The method consists in subjecting the plate to a hardening, in rolling heat or after austenitization in a furnace; cooling the plate at a cooling speed higher than 0.5 °C/s between a temperature higher than AC3 and a temperature ranging between T = 800 - 270xC* - 90xMn -37xNi - 70XCr - 83x(Mo + W/2) and T-50 °C; then cooling the plate at a core cooling speed Vr < 1150xep-1.7 between temperature T and 100 °C (ep = plate temperature expressed in mm); cooling the plate down to room temperature and, optionally planishing. The invention also concerns the resulting plate.

Description

METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND SHEET OBTAINED

The present invention relates to an abrasion-resistant steel and its method of manufacture.

High abrasion resistant steels with a hardness of about 600 Brinell are known. These steels contain from 0.4% to 0.6% of carbon and from 0.5% to 3% of at least one alloying element such as manganese, nickel, chromium and molybdenum and are soaked to have a completely martensitic structure. But these steels are very difficult to weld and cut. To overcome these drawbacks, it has been proposed, especially in EP 0 739 993, to use for the same uses, a less hard steel, whose carbon content is about 0.27% and having a quenched structure containing a significant amount of residual austenite. But these steels are still difficult to weld or cut.

The object of the present invention is to overcome these disadvantages, by proposing an abrasion-resistant steel sheet whose abrasion resistance is comparable to that of known steels but whose weldability and thermal cutting ability is better.

For this purpose, the subject of the invention is a method for manufacturing a part, and in particular a sheet, made of steel for abrasion, the chemical composition of which comprises, by weight:

0.24% <C <0.35% 0% <If <2%

0% <Al <2%

0.5% <Si + Al <2%

0% <Mn <2.5%

0% <Ni <5% 0% <Cr <5%

0% <Mo <1%

0% <W <2%

0.1% <Mo + W / 2 <1%

0% <Cu <1.5% 0% <B <0.02%

0% <Ti 1, 1%

0% <Zr <2,2%

0.35% <Ti + Zr / 2 <1, 1% 0% <S <0.15%

N <0.03%

optionally at least one element selected from Nb, Ta and V in contents such that Nb / 2 + Ta / 4 + V <0.5%,

- optionally at least one element selected from Se, Te, Ca, Bi, Pb in contents less than or equal to 0.1%, the balance being iron and impurities resulting from the elaboration, the chemical composition further satisfying the following relationships:

C * = C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095% and preferably> 0.12% and: 1, 05xMn + 0.54xNi + 0.50xCr + 0.3x (Mo + W / 2 ) ^1/2 + K> 1, 8 or better 2 with: K = 0.5 if B> 0.0005% and K = 0 if B <0.0005%.

According to this method, the part or the sheet is subjected to a quenching heat treatment, carried out in hot hot forming such as rolling or after austenitization by reheating in an oven, which consists in: - cooling the sheet to an average cooling rate greater than 0.5 ° C / s between a temperature above AC ₃ and a temperature between T = 800 - 270xC * - 90xMn -37xNi - 70XCr - 83x (Mo + W / 2) and T - 50 ° C, the temperature being expressed in ° C and the contents of C *, Mn, Ni, Cr, Mo and W, being expressed in% by weight, - then cool the sheet at a mean cooling rate at heart Vr < 1150xep ^"1 (in ° C / s) and greater than 0.1 ° C / s between the temperature T and 100 ° C, ep being the thickness of the sheet expressed in mm,

- And to cool the sheet to room temperature, optionally, it performs a planing. Optionally, quenching may be followed by tempering at a temperature below 350 ° C, and preferably below 250 ° C.

The invention also relates to a sheet obtained in particular by this method, the steel having a martensitic or martensito-bainitic structure, said structure containing from 5% to 20% retained austenite, as well as carbides. The thickness of the sheet may be between 2 mm and 150 mm and its flatness is characterized by an arrow less than or equal to 12 mm / m and preferably less than 5 mm / m.

The invention will now be described in a more precise but nonlimiting manner and be illustrated by examples. To manufacture a sheet according to the invention, a steel is produced whose chemical composition comprises, in% by weight:

from 0.24% to 0.35% of carbon to allow the formation of a large quantity of carbides and to obtain a sufficient hardness, while having a sufficient welding ability; preferably, the carbon content is less than 0.325%, and more preferably less than 0.3%.

From 0% to 1.1% titanium, from 0% to 2.2% zirconium. The sum Ti + Zr / 2 must be greater than 0.35% and preferably greater than 0.4%, and more preferably greater than 0.5%, so as to form a large amount of large carbides. However, this sum must remain less than 1.1% so as to keep enough carbon in solution in the matrix after formation of carbides. Preferably this sum must remain less than 1%, and better still 0.9% and better still less than 0.7% if one needs to favor the tenacity of the material. As a result, the titanium content should preferably remain less than 1%, and more preferably less than 0.9%, or even less than 0.7%, and the zirconium content should preferably remain below 2%, and better less than 1, 8%, or even less than 1, 4%.

From 0% (or traces) to 2% silicon and 0% (or traces) at 2% aluminum, the sum Si + Al being between 0.5% and 2% and preferably greater than 0.7%. These elements, which are deoxidizing agents, also have the effect of favoring the obtaining of a metastable retained austenite highly loaded with carbon whose transformation into martensite is accompanied by a significant swelling favoring the anchoring of the titanium carbides or of zirconium.

- From 0% (or traces) to 2% or even 2.5% of manganese, from 0% (or traces) to 4% or even 5% of nickel and 0% (or traces) at 4% or even 5% of chromium, to obtain a sufficient quenchability and to adjust the different mechanical characteristics or use. Nickel has a particularly favorable effect on toughness, but this element is expensive. Chromium also forms fine carbides in martensite or bainite. From 0% (or traces) to 1% molybdenum and 0% (or traces) at 2% tungsten, the sum Mo + W / 2 being between 0.1% and 1%, and preferably remains less than 0.8%, or better, less than 0.6%. These elements increase the quenchability and form in martensite or bainite of hardening carbides, in particular by self-precipitation during cooling. It is not necessary to exceed a molybdenum content of 1% in order to obtain the desired effect, particularly as regards the precipitation of hardening carbides. Molybdenum can be replaced in whole or in part by a double weight of tungsten. However, this substitution is not sought in practice because it offers no advantage over molybdenum and is more expensive.

- Possibly from 0% to 1.5% copper. This element can provide additional hardening without damaging the weldability. Above 1, 5%, it has no significant effect, it generates hot rolling difficulties and unnecessarily expensive.

0% to 0.02% boron. This element can be added optionally to increase quenchability. For this effect to be obtained, the boron content should preferably be greater than 0.0005% or better 0.001%, and need not exceed substantially 0.01%. - Up to 0.15% sulfur. This element is a residual usually limited to 0.005% or less, but its content can be voluntarily increased to improve machinability. It should be noted that in the presence of sulfur, in order to avoid difficulties of hot transformation, the manganese content must be greater than 7 times the sulfur content. - Possibly at least one element taken from niobium, tantalum and vanadium, in such contents that Nb / 2 + Ta / 4 + V remains less than 0.5% in order to form relatively large carbides which improve the resistance to abrasion. But the carbides formed by these elements are less effective than those formed by titanium or zirconium, that is why they are optional and added in limited quantities.

- Possibly one or more elements selected from selenium, tellurium, calcium, bismuth and lead in contents of less than 0.1% each. These elements are intended to improve machinability. Note that when the steel contains Se and / or Te, the manganese content must be sufficient sulfur content to form selenides or tellurides of manganese.

- The rest being iron and impurities resulting from the elaboration. Among the impurities, there is in particular nitrogen, the content of which depends on the production process but generally does not exceed 0.03%. This element can react with titanium or zirconium to form nitrides which must not be too big to not deteriorate toughness. In order to avoid the formation of large nitrides, titanium and zirconium can be added to the liquid steel in a very gradual manner, for example by contacting the oxidized liquid steel with an oxidized phase such as a slag loaded with oxides of titanium or zirconium, then deoxidizing the liquid steel, so as to slowly diffuse titanium or zirconium from the oxidized phase to the liquid steel.

In addition, in order to obtain satisfactory properties, the carbon, titanium, zirconium and nitrogen contents must be such that: C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095%

The expression C - Ti / 4 - Zr / 8 + 7xN / 8 = C * represents the free carbon content after precipitation of the titanium and zirconium carbides, taking into account the formation of titanium and zirconium nitrides. This free carbon content C * must be greater than 0.095%, and preferably> 0.12%, to have a martensite having a minimum hardness. The lower this content, the better the welding and thermal cutting ability.

In addition, the chemical composition must be chosen so that the quenchability of the steel is sufficient, given the thickness of the sheet that is to be manufactured. For that, the chemical composition must satisfy the relation: Tremp = 1, 05xMn + 0,54xNi + 0,50xCr + 0,3x (Mo + W / 2) ^1/2 + K> 1, 8 or better 2 with: K = 0.5 if B> 0.001% and K = 0 if B <0.001%,

In addition, and to obtain a good resistance to abrasion, the micrographic structure of the steel consists of martensite or bainite or a mixture of these two structures, and from 5% to 20% retained austenite. This structure further comprises large titanium or zirconium carbides formed at high temperature, or even carbides of niobium, tantalum or vanadium. The inventors have found that the effectiveness of large carbides for improving the abrasion resistance could be obelated by the premature loosening thereof and that this loosening could be avoided by the presence of metastable austenite which is transformed under the effect of abrasion phenomena. As the transformation of the metastable austenite is by swelling, this transformation in the abraded underlayer increases the resistance to carburetion and thus improves abrasion resistance. On the other hand, the high hardness of the steel and the presence of embrittling titanium carbides make it necessary to limit the leveling operations as much as possible. From this point of view, the inventors have found that by slowing down cooling sufficiently in the bainitomensitic transformation domain, the residual deformations of the products are reduced, which makes it possible to limit the leveling operations. The inventors have found that cooling the workpiece or sheet at a cooling rate Vr <1150xep ^"1.7 , (in this formula, ep is the thickness of the sheet expressed in mm, and the cooling rate is expressed in ° C / s) below a temperature T = 800 - 270xC * - 90xMn -37xNi - 70XCr - 83x (Mo + W / 2), (expressed in ° C), on the one hand, a proportion was obtained significant residual austenite, and on the other hand, the residual stresses generated by the phase changes are reduced.This reduction of stress is desirable, both to limit the use of leveling or to facilitate it on the one hand, and to limit the risk of cracking during subsequent welding and bending operations To manufacture a sheet having a good resistance to abrasion and well flat, the steel is produced, it is cast as slab or ingot. The slab or slug is hot rolled to obtain a sheet that is submitted to a heat treatment allowing at the same time to obtain the desired structure and a good flatness without subsequent planing or with limited planing. The heat treatment can be carried out directly in the hot rolling or carried out later, and possibly after a cold planing or half-hot.

To carry out the heat treatment: - Either directly after hot rolling, or after reheating above point AC ₃ , the sheet is cooled to an average cooling rate, greater than 0.5 ° C./s. say higher than the critical bainitic transformation rate to a temperature equal to or slightly less than a temperature T = 800 - 270xC * - 90xMn -37xNi - 70XCr - 83x (Mo + W / 2), (expressed in ° C), in order to avoid the formation of ferritic constituents or pearlitic. By slightly lower is meant a temperature between T and T - 50 ° C, or better still between T and T - 25 ° C, or better still, between T and T - 10 ° C.

then, between the previously defined temperature and approximately 100 ° C., the sheet is cooled to a mean core cooling rate Vr of between 0.1 ° C./sec, to obtain a sufficient hardness, and 1150xep ^{"1, 7} , to obtain the desired structure,

and the sheet is cooled to room temperature, preferably, but not necessarily, at a slow speed.

In addition, an expansion treatment, such as tempering, can be carried out at a temperature of less than or equal to 350 ° C, and preferably less than 250 ° C.

This gives a sheet, whose thickness can be between 2 mm and 150 mm, having excellent flatness characterized by an arrow less than 12 mm per meter without planing, or with a moderate leveling. The sheet has a hardness of between 280HB and 450HB, approximately. This hardness depends mainly on the free carbon content C * = C - Ti / 4 - Zr / 8 + 7xN / 8.

By way of example, steel sheets identified A to C according to the invention and D to E according to the prior art were produced. The chemical compositions of the steel, expressed as 10 ^"3 wt%, and the hardness and an index of wear resistance Rus, are reported in Table 1. The wear resistance was measured by weight loss of a prismatic test tube rotated in a tank containing calibrated granules of quartzite for 5 hours.

The Rus index of a steel is equal to 100 times the ratio of the wear resistance of the steel in question and the wear resistance of a reference steel (steel D). Thus, a steel whose Rus = 110 index has a wear resistance 10% higher than that of the reference steel.

All sheets are 27 mm thick and are hardened after austenitization at 900 ° C. After austenitisation: - for steel sheets A and C, the average cooling rate is 7 ° C / s above the temperature T defined above, and 1 6 ° C / s below, in accordance with 'invention; for sheet B, the average cooling rate is 0.8 ° C / s above the temperature T defined above, and 0.15 ° C / s below, according to the invention; the steel sheets D and E, given for comparison, were cooled at an average speed of 24 ° C / s above the temperature T defined above, and at an average speed of 12 ° C / s below .

Table 1

containing from 5% to 20% retained austenite and large titanium carbides, while the plates given for comparison have a completely martensitic structure.

The comparison of the wear resistances and the hardnesses shows that, although being very substantially less hard than the sheets given for comparison, the sheets according to the invention have a slightly better resistance to wear. The comparison of the free carbons shows that the good abrasion resistance of the sheets according to the invention is obtained with very significantly lower free carbons, which leads to significantly better welding or thermal cutting abilities than for the sheets according to the invention. the prior art. Furthermore, the deformation after cooling, without planing, for steels according to the invention A to C is about 5 mm / m and 16 mm / m for steels D and E given for comparison. These results show the reduction of deformation of the products obtained thanks to the invention. This results in practice, according to the degree of requirement in flatness of the users,

- the possibility of delivering products without planing, which generates a cost saving and a reduction in residual stresses,

- Or performing a planing to meet a more severe flatness requirement (for example 5mm / m) but performed more easily and introducing fewer constraints due to the original deformation less on the products according to the invention.

Claims

1 - Process for producing an abrasion-resistant steel part or sheet whose chemical composition comprises, by weight: 0.24% <C <0.35%

0% <If <2%

0% <Al <2%

0.5% <Si + Al <2%

0% <Mn <2.5% 0% <Ni <5%

0% <Cr <5%

0% <Mo <1%

0% <W <2%

0.1% <Mo + W / 2 <1% 0% <B <0.02%

0% <Ti <1.1%

0% <Zr <2.2%

0.35% <Ti + Zr / 2 <1.1%

0% <S <0.15% N <0.03%

optionally from 0% to 1.5% copper,

C * = C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095% and: 1, 05xMn + 0.54xNi + 0.50xCr + 0.3x (Mo + W / 2) ^1/2 + K> 1 , 8 with K = 0.5 if B> 0.0005% and K = 0 if B <0.0005%, according to which the sheet is subjected to a quenching heat treatment, carried out in the hot forming hot and for example rolling or after austenitization by reheating in an oven, to carry out the quenching: the part or sheet is cooled to an average cooling rate greater than 0.5 ° C./s between a temperature greater than AC ₃ and a temperature between T = 800 - 270 × C * - 90 × Mn-37 × Ni-70 × C-83 × ( Mo + W / 2), and T-50 ° C approximately, then the part or the sheet is cooled to an average core cooling rate Vr <1150xep ^"1.7 and greater than 0.1 ° C / s between the temperature T and 100 ° C, ep being the thickness of the sheet expressed in mm, the piece or sheet is cooled to room temperature and optionally planing is carried out.

2 - Process according to claim 1, characterized in that:

1, 05xMn + 0.54xNi + 0.50xCr + 0.3x (Mo + W / 2) ^1/2 + K> 2

3 - Process according to claim 1 or claim 2, characterized in that:

Ti + Zr / 2> 0.4%

4 - Process according to any one of claims 1 to 3, characterized in that:

C *> 0.12%

5 - Process according to any one of claims 1 to 4, characterized in that:

If + Al> 0.7%

6 - Process according to any one of claims 1 to 5, characterized in that, in addition, is carried out at a temperature less than or equal to 350 ° C.

7 - Process according to any one of claims 1 to 6, characterized in that to add the titanium in the steel, the liquid steel is placed in contact with a slag containing titanium and the titanium is slowly diffused from slag in liquid steel.

8 - Part, and in particular sheet metal, abrasion-resistant steel whose chemical composition comprises, by weight:

0.24% <C <0.35% 0% <If <2% 0% <Al <2%

0.5% <Si + Al <2%

0% <Mn <2.5%

0% <Ni <5% 0% <Cr <5%

0% <Mo <1%

0% <W <2%

0.1% <Mo + W / 2 1%

0% <B <0.02% 0% <Ti <1.1%

0% <Zr <2.2%

0.35% <Ti + Zr / 2 <1.1%

0% <S <0,15%

N <0.03% - optionally from 0% to 1.5% copper,

C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095% and:

1, 05xMn + 0.54xNi + 0.50xCr + 0.3x (Mo + W / 2) ¹² + K> 1, 8 with: K = 0.5 if B> 0.0005% and K = 0 if B < 0.0005%, the steel having a martensitic or martensite-bainitic structure, the said structure containing from 5% to 20% retained austenite and carbides.

9 - Part according to claim 8, characterized in that: 1, 05xMn + 0.54xNi + 0.50xCr + 0.3x (Mo + W / 2) ¹² + K> 2

10 - part according to claim 8 or claim 9, characterized in that:

Ti + Zr / 2> 0.4% 11 - part any one of claims 8 to 10, characterized in that:

C *> 0.12%

12 - part any one of claims 8 to 11, characterized in that:

If + Al> 0.7%

13 - part according to any one of claims 8 to 12, characterized in that it is a sheet of thickness between 2 mm and 150 mm.