RU2803534C1 - Wear-resistant steel sheet and method for manufacturing wear-resistant steel sheet - Google Patents

Abstract

FIELD: metallurgy.

SUBSTANCE: invention relates to the wear-resistant steel sheet used as a material for the manufacture of parts of industrial and transport equipment used in the fields of construction, civil engineering, mining, etc. The sheet has a chemical composition containing in wt.%: C: more than 0.3 and 0.45 or less, Si: 0.05 - 1.00, Mn: 0.50 - 2.00 P: 0.020 or less, S: 0.010 or less Al: 0.01 - 0.06, Cr: 0.10 - 1.00, N: 0.0100 or less, optionally at least one element selected from the group consisting of: Nb: 0.005 - 0.020 Ti: 0.005 - 0.020 and B: 0.0003 - 0.0030, optionally at least one element selected from the group consisting of: Cu: 0.01 - 0.5 Ni: 0.01 - 3.0 Mo: 0.1 - 1.0 V: 0.01 - 0.10W: 0.01 - 0.5 and Co: 0.01 - 0.5, optionally at least one element selected from the group consisting of: Ca: 0.0005 - 0.0050 Mg: 0.0005 - 0.0100 and REM: 0.0005–0.0200%, the rest is Fe and unavoidable impurities. The volume fraction of martensite at a depth of 1 mm from the surface of the wear-resistant steel sheet is 90% or more. Brinell hardness at a depth of 1 mm from the surface is 500 - 650 HBW 10/3000. The difference in Vickers hardness in the transverse direction is 30Hv10 or less, and said difference in hardness in the transverse direction is defined as the difference in hardness at a depth of 1 mm from the surface between two adjacent points with an interval of 10 mm in the transverse direction of the wear-resistant steel sheet.

EFFECT: sheet has the desired combination of abrasion resistance and flex workability.

6 cl, 3 tbl

Description

Field of technology

The present invention relates to a wear-resistant steel sheet, and in particular relates to a wear-resistant steel sheet having suitable wide strip bending machinability and suitable for industrial and transportation equipment parts used in the fields of construction, civil engineering, mining, etc. The present invention also relates to a method for producing wear-resistant steel sheet. The term “wide strip bending machinability” in the present disclosure refers to the bending machinability of a steel sheet with a width of 200 mm or more, which is a problem in actual use.

State of the art

It is known that the abrasion resistance of steel material is improved by increasing its hardness. Consequently, steel materials subjected to heat treatment such as hardening to increase hardness are used in parts subject to abrasion by earth and sand, stones, etc.

For example, JP S63-169359 A (PTL 1) describes a method for producing a wear-resistant steel sheet by hot rolling a steel material having a certain chemical composition to produce a steel sheet and then quenching the steel sheet. By the method described in PTL 1, by controlling the content of C, alloying elements and N, a wear-resistant steel sheet is obtained which has a hardness of 340 HB or more and high toughness after quenching, and has improved weld resistance to low-temperature cracking.

JP S64-031928 A (PTL 2) describes a method of producing wear-resistant steel sheet by hot rolling steel having a specified chemical composition at a temperature of 900°C to the Ar3 transformation point with a reduction ratio of 15% or higher and then directly quenching the resulting steel sheet from temperature Ar3 transformation point or higher. Using the method described in PTL 2, by controlling the chemical composition and quenching conditions, a wear-resistant steel sheet with high hardness can be easily obtained.

The corresponding methods described in PTL 1 and PTL 2 improve abrasion resistance by increasing hardness. Meanwhile, the demand for wear-resistant steels, which are excellent not only in abrasion resistance but also in bending machinability, is also growing, for use in parts of various shapes and reducing weld areas.

In response to such demand, for example, JP H07-090477 A (PTL 3) offers wear-resistant steel containing, in wt.%, C: 0.05 - 0.20%, Mn: 0.50 - 2.5% and Al: 0.02 - 2.00% and having a martensite area ratio of 5% or more and 50% or less. According to PTL 3, hot-rolled steel is heated to a temperature in the ferrite-austenite two-phase region between Ac1 and Ac3, and then rapidly cooled to control the martensite area fraction, resulting in a wear-resistant steel with adequate machinability and weldability.

JP 2006-104489 A (PTL 4) proposes a method of producing wear-resistant steel sheet by hot rolling steel having a certain chemical composition, followed by directly cooling the resulting steel sheet to Ms ± 25°C, interrupting the cooling and heating the steel sheet to Ms +. 50°C or more and then cooling the steel sheet to room temperature. According to PTL 4, the minimum hardness in the area from the surface to 5 mm in depth of the steel sheet produced by this manufacturing method is at least 40HV less than the maximum hardness in the deeper region of the steel sheet, and thus the bending processability is improved .

JP 2008-169443 A (PTL 5) proposes a method for producing a wear-resistant steel sheet by hot rolling steel having a certain chemical composition with a DI* (hardenability index) of 60 or more, and then cooling the resulting steel sheet to a temperature of 400°C or less. at an average cooling rate of 0.5 - 2°C/s. According to PTL 5, 400 particles/mm ² or more of Ti-based carbide with an average particle size of 0.5 - 50 μm are released in the wear-resistant steel sheet produced by this manufacturing method, and thus the wear-resistant steel has suitable abrasion resistance and bending workability, obtained without heat treatment.

List of cited sources

Patent literature

PTL 1: JP S63-169359 A

PTL 2: JP S64-031928 A

PTL 3: JP H07-090477 A

PTL 4: JP 2006-104489 A

PTL 5: JP 2008-169443 A

Disclosure of the invention

Technical problem

As described in PTL 3 to PTL 5, traditional methods for improving the flexural workability of a wear-resistant steel sheet are based on the consideration that by providing flexural workability by limiting the hardness of the steel sheet matrix, abrasion resistance is improved by controlling the microstructure or carbide precipitation. Using such methods, it is difficult to sufficiently improve the hardness of the matrix, making it impossible to achieve both abrasion resistance and flexural workability.

Given that the need for abrasion resistance is increasing from year to year, there is a need for a method that can provide high levels of both abrasion resistance and flexural workability, which are mutually contradictory properties.

When processing wear-resistant steel sheet to produce a finished product such as civil engineering and construction equipment parts, bending work is generally carried out under the condition that the width of the wear-resistant steel sheet is 200mm or more. Since flexural cracks are generally more likely when the sheet width is larger, it is necessary to use steel sheet with a sheet width of 200mm or more to evaluate the flexural workability of the steel sheet in actual use. However, the bending ability of a sheet with a width of 200 mm or more is not taken into account in the above-described conventional methods.

Thus, it may be useful to provide a wear-resistant steel sheet suitable for both abrasion resistance and flexural workability, which are mutually contradictory properties. With regard to bending workability, in particular, it may be useful to provide a wear-resistant steel sheet having suitable bending workability under severe conditions when the width of the steel sheet is 200 mm or more (hereinafter referred to as “broad strip bending workability”).

Solution

We have studied each factor affecting the machinability of wear-resistant steel sheet in wide strip bending, and as a result have established the following (1) - (4).

(1) The bending machinability of wear-resistant steel sheet largely depends on the hardness and ductility of the surface layer of the wear-resistant steel sheet.

(2) In particular, if the wear-resistant steel sheet has a locally hardened zone or softening zone, the deformation is concentrated around the softening zone or hardening zone, and the ductility is reduced, so that the bending machinability of the wide strip is reduced.

(3) By reducing the difference in hardness of wear-resistant steel sheet, the bending machinability of wide strip can be improved without reducing the hardness of the matrix, which greatly affects the abrasion resistance.

(4) By producing wear-resistant steel sheet by carrying out quenching in the austenitic temperature range and reducing the difference in cooling rate in the transverse direction of the steel sheet during quenching, the difference in hardness of the wear-resistant steel sheet can be reduced.

This disclosure is based on these data and further research. Therefore, we propose the following.

1. Wear-resistant steel sheet including a chemical composition containing (consisting of), in mass%, C: more than 0.30% and 0.45% or less, Si: 0.05 - 1.00%, Mn: 0 .50 - 2.00%, P: 0.020% or less, S: 0.010% or less, Al: 0.01 - 0.06%, Cr: 0.10 - 1.00% and N: 0.0100% or less, the rest is Fe and inevitable impurities, in which the volume fraction of martensite at a depth of 1 mm from the surface of the wear-resistant steel sheet is 90% or more, the hardness at a depth of 1 mm from the surface is 500 - 650 HBW 10/3000 Brinell, and the difference The transverse hardness is 30Hv10 or less Vickers, and the transverse hardness difference is defined as the difference in hardness at a depth of 1 mm from the surface of the wear-resistant steel sheet between two adjacent points, with an interval of 10 mm in the transverse direction.

2. Wear-resistant steel sheet according to claim 1, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Nb: 0.005 - 0.020%, Ti: 0.005 - 0.020% and B: 0.0003 - 0.0030%.

3. Wear-resistant steel sheet according to claims. 1 or 2, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Cu: 0.01 - 0.5%, Ni: 0.01 - 3.0%, Mo: 0.1 - 1.0%, V: 0.01 - 0.10%, W: 0.01 - 0.5% and Co: 0.01 - 0.5%.

4. Wear-resistant steel sheet according to any one of paragraphs. 1 - 3, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Ca: 0.0005 - 0.0050%, Mg: 0.0005 - 0.0100% and REM: 0.0005 - 0.0200%.

5. A method for producing wear-resistant steel sheet, comprising: heating the steel material to a heating temperature that corresponds to the transformation point of Ac3 or higher, and 1300°C or lower, wherein the steel material has a chemical composition containing, in wt.%: C: more than 0.30 % and 0.45% or less, Si: 0.05 - 1.00%, Mn: 0.50 - 2.00%, P: 0.020 or less, S: 0.010 or less, Al: 0.01 - 0 .06%, Cr: 0.10 - 1.00% and N: 0.0100% or less, the rest being Fe and inevitable impurities; hot rolling the heated steel material to obtain a hot rolled steel sheet; and subjecting the hot-rolled steel sheet to quenching, wherein the quenching is (a) direct quenching by cooling the hot-rolled steel sheet from a cooling start temperature that is a transformation point of Ar3 or higher to a cooling stopping temperature that is Mf or lower, or (b ) reheating, cooling quenching of the hot-rolled steel sheet, reheating the cooled hot-rolled steel sheet to the reheating temperature, which is the transformation point of Ac3 or higher, and 950°C or less, and cooling the reheated hot-rolled steel sheet from the reheating temperature to the finishing temperature cooling equal to point Mf or lower, and in the quenching cooling process, the difference in the average cooling rate between the center position and the 1/4 position in the transverse direction of the hot-rolled steel sheet, and the difference in the average cooling rate between the center position and the 3/4 position in the transverse direction direction of the hot-rolled steel sheet is 5°C/s or less.

6. A method for manufacturing a wear-resistant steel sheet according to claim 5, in which the end temperature of cooling during quenching is lower (point Mf - 100°C), and the method includes, after quenching, tempering of a hardened hot-rolled steel sheet at a tempering temperature equal to (point Mf - 80° C) or higher and (point Mf + 50°C) or lower.

7. The method for manufacturing wear-resistant steel sheet according to claim 6, wherein when tempering, the hardened hot-rolled steel sheet is kept at the tempering temperature for 60 seconds or more.

8. Method of manufacturing wear-resistant steel sheet according to claims. 6 or 7, in which the average heating rate during tempering is 2°C/s or more.

9. The method for manufacturing a wear-resistant steel sheet according to claim 5, wherein the cooling end temperature during quenching is Mf point or less and (Mf point is 100°C) or more, and the method includes air cooling of the hardened hot-rolled steel sheet after quenching.

10. A method for manufacturing wear-resistant steel sheet according to any one of paragraphs. 5 - 9, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Nb: 0.005 - 0.020%, Ti: 0.005 - 0.020% and B: 0.0003 - 0.0030%.

11. A method for manufacturing wear-resistant steel sheet according to any one of claims. 5 - 10, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Cu: 0.01 - 0.5%, Ni: 0.01 - 3.0%, Mo: 0.1 - 1.0%, V: 0.01 - 0.10%, W: 0.01 - 0.5% and Co: 0.01 - 0.5%.

12. A method for manufacturing wear-resistant steel sheet according to any one of paragraphs. 5 - 11, the chemical composition of which additionally contains in % wt. one or more elements selected from the group consisting of Ca: 0.0005 - 0.0050%, Mg: 0.0005 - 0.0100% and REM: 0.0005 - 0.0200%.

Positive effect

In this way, it is possible to produce a wear-resistant steel sheet having suitable both abrasion resistance and wide strip bending workability. Since suitable bending machinability of wide strip can be achieved without reducing hardness, which affects abrasion resistance, today's high level of abrasion resistance requirements can be achieved. The wear-resistant steel sheet according to the present invention is thus suitable as a material for industrial equipment components and transportation equipment used in construction, civil engineering, mining, etc.

Carrying out the invention

Embodiments of the present disclosure will now be described in detail. The following description provides examples of preferred embodiments of the present disclosure and does not limit the scope of the present disclosure.

Chemical composition

In the present disclosure, it is important that the wear-resistant steel sheet and the steel material used in making the wear-resistant steel sheet have the above-described chemical composition. First, the reasons for limiting the chemical composition of steel as described above in the present specification will be described below. In the specification, "%" in relation to chemical composition means % by weight unless otherwise indicated.

C: more than 0.30% and 0.45% or less

C is an element that increases matrix hardness and improves abrasion resistance. To achieve this effect, the C content is more than 0.30%. The C content is preferably 0.35% or more. When the C content is more than 0.45%, the hardness of the matrix increases excessively and the workability when bending a wide strip is significantly reduced. Therefore, the C content is 0.45% or less. The C content is preferably 0.43% or less.

Si: 0.05 - 1.00%

Si is an element that acts as a deoxidizing agent. Si also increases the hardness of the matrix due to solid solution strengthening of the steel. When the Si content is less than 0.05%, the deoxidation effect is insufficient and the number of inclusions increases, resulting in a decrease in ductility. Therefore, the Si content is 0.05% or more. The Si content is preferably 0.10% or more, or more preferably 0.20% or more. When the Si content is more than 1.00%, the number of inclusions increases and ductility decreases, as a result, the workability when bending a wide strip decreases. Therefore, the Si content is 1.00% or less. The Si content is preferably 0.80% or less, or more preferably 0.60% or less.

Mn: 0.50 - 2.00%

Mn is an element that increases matrix hardness and improves abrasion resistance. If the Mn content is less than 0.50%, the hardening ability is insufficient and uniform hardness cannot be achieved. Therefore, the Mn content is 0.50% or more. The Mn content is preferably 0.60% or more, or more preferably 0.70% or more. If the Mn content exceeds 2.00%, the hardness increases excessively, so that the bending machinability of the wide strip is deteriorated. Therefore, the Mn content is 2.00% or less. The Mn content is preferably 1.80% or less, or more preferably 1.60% or less.

P: 0.020% or less

P is an element contained as an unavoidable impurity and causing adverse effects such as segregation at grain boundaries and acting as a source of destruction. Accordingly, it is desirable to reduce the P content as much as possible, but 0.020% or less is acceptable. Although there is no lower limit for P content, reducing P content to less than 0.001% is difficult on an industrial scale. Therefore, the P content is preferably 0.001% or more from the viewpoint of performance.

S: 0.010% or less

S is an element contained as an unavoidable impurity and having an adverse effect, for example, when contained in steel in the form of sulfide-based inclusions such as MnS, and acting as a source of destruction. Accordingly, it is desirable to reduce the sulfur content as much as possible, but 0.010% or less is acceptable. Although no lower limit has been established for the S content, reducing the S content to less than 0.0001% is difficult on an industrial scale. Therefore, the S content is preferably 0.0001% or more from the viewpoint of performance.

Al: 0.01 - 0.06%

Al is an element that acts as a deoxidizing agent and also forms a nitride to refine crystal grains and improve ductility. To achieve these effects, the Al content is 0.01% or more. When the Al content is more than 0.06%, excessive nitride formation occurs and an increase in surface defects occurs. When the Al content is more than 0.06%, the content of oxide-based inclusions increases and ductility decreases, as a result of which the bending workability of the wide strip decreases. Therefore, the Al content is 0.06% or less. The Al content is preferably 0.05% or less, or more preferably 0.04% or less.

Cr: 0.10 - 1.00%

Cr is an element that increases matrix hardness and improves abrasion resistance. If the Cr content is less than 0.10%, the hardening effect of adding Cr cannot be achieved, and uniform hardness cannot be obtained. Therefore, the Cr content is 0.10% or more. The Cr content is preferably 0.20% or more preferably 0.25% or more. When the Cr content is more than 1.00%, the ductility decreases due to the formation of precipitates and the workability when bending a wide strip deteriorates. Therefore, the Cr content is 1.00% or less. The Cr content is preferably 0.85% or less, or more preferably 0.80% or less.

N: 0.0100% or less

N is an element contained as an unavoidable impurity and forms nitrides etc., and thus contributes to the refinement of crystal grains. However, if the formation of precipitates is excessive, the ductility is reduced and the bending workability of the wide strip is deteriorated. Therefore, the N content is 0.0100% or less. The N content is preferably 0.0060% or less, or more preferably 0.0040% or less. Although there is no lower limit for N content, reducing N content to less than 0.0010% is difficult on an industrial scale. Therefore, the N content is preferably 0.0010% or more from the point of view of productivity.

The wear-resistant steel sheet and steel material according to one embodiment of the present invention has a chemical composition containing the above-described components, and the balance is Fe and inevitable impurities.

In another embodiment of the present invention, the chemical composition may optionally further contain one or more elements selected from the group consisting of Nb: 0.005 - 0.020%, Ti: 0.005 - 0.020% and B: 0.0003 - 0.0030%.

Nb: 0.005 - 0.020%

Nb is an element that increases matrix hardness and further improves abrasion resistance. Nb also forms carbonitride and refines former austenite grains. In the case of adding Nb to achieve these effects, the Nb content is 0.005% or more, and preferably 0.007% or more. When the Nb content is more than 0.020%, NbC is released in large quantities and ductility is reduced, resulting in reduced bending workability of the wide strip. Accordingly, in the case of adding Nb, the Nb content is 0.020% or less. The Nb content is preferably 0.018% or less.

Ti: 0.005 - 0.020%

Ti is an element that forms nitride in steel and refines former austenite grains, thereby improving ductility. In the case where Ti and B coexist, resulting in Ti fixing N, the precipitation of BN is suppressed, and the hardenability effect can be enhanced by B. In the case of adding Ti to achieve these effects, the Ti content is 0.005% or more. The Ti content is preferably 0.007% or more. If the Ti content exceeds 0.020%, solid TiC precipitates in large quantities, causing a decrease in wide strip bending machinability. Accordingly, in the case of adding Ti, the Ti content is 0.020% or less. The Ti content is preferably 0.015% or less.

B: 0.0003 - 0.0030%

B is an element that significantly improves hardenability even when added in small quantities. By adding B, the formation of martensite can be stimulated and the abrasion resistance can be improved more effectively. In the case of adding B to achieve this effect, the B content is 0.0003% or more. The B content is preferably 0.0005% or more, or more preferably 0.0008% or more. If the B content is more than 0.0030%, an unfavorable effect occurs such as the formation of a large amount of precipitates such as borides, which act as a source of destruction. Accordingly, in the case of adding B, the content of B is 0.0030% or less. The B content is preferably 0.0015% or less.

In another embodiment of the present invention, the chemical composition may optionally further contain one or more elements selected from the group consisting of Cu: 0.01 - 0.5%, Ni: 0.01 - 3.0%, Mo: 0.1 - 1.0%, V: 0.01 - 0.10%, W: 0.01 - 0.5% and Co: 0.01 - 0.5%.

Cu: 0.01 - 0.5%

Cu is a hardenability improving element and can optionally be added to further increase hardness. In the case of adding Cu to achieve this effect, the Cu content is 0.01% or more. When the copper content is more than 0.5%, surface defects occur, which leads to reduced productivity. In addition, the cost of the alloy increases. Accordingly, in the case of adding Cu, the Cu content is 0.5% or less.

Ni: 0.01 - 3.0%

Ni is a hardenability improving element and can optionally be added to further increase hardness. In the case of adding Ni to achieve this effect, the Ni content is 0.01% or more. When the Ni content is more than 3.0%, the cost of the alloy increases. Accordingly, the Ni content is 3.0% or less.

Mo: 0.1 - 1.0%

Mo is a hardenability improving element and can optionally be added to further increase hardness. In the case of adding Mo to achieve this effect, the content of Mo is 0.1% or more. If the Mo content exceeds 1.0%, weldability deteriorates and the cost of the alloy increases. Accordingly, in the case of adding Mo, the content of Mo is 1.0% or less.

V: 0.01 - 0.10%

V is a hardenability improving element and can optionally be added to further increase hardness. V is also released as VN and thus helps reduce dissolved nitrogen. In the case of adding V to achieve these effects, the V content is 0.01% or more. If the V content is more than 0.10%, solid VC is released, causing a decrease in ductility. Accordingly, in the case of adding V, the content of V is 0.10% or less, preferably 0.08% or less, or more preferably 0.05% or less.

W: 0.01 - 0.5%

W is a hardenability improving element, as in the case of Mo, and may optionally be added. In the case of adding W to achieve this effect, the W content is 0.01% or more. When the W content is more than 0.5%, the cost of the alloy increases. Accordingly, in the case of adding W, the W content is 0.5% or less.

Co: 0.01 - 0.5%

Co is a hardenability improving element and may optionally be added. In the case of adding Co to achieve this effect, the Co content is 0.01% or more. When the Co content is more than 0.5%, the cost of the alloy increases. Accordingly, in the case of adding Co, the Co content is 0.5% or less.

In another embodiment of the present invention, the chemical composition may optionally further contain one or more elements selected from the group consisting of Ca: 0.0005 - 0.0050%, Mg: 0.0005 - 0.0100% and REM: 0.0005 - 0.0200%.

Ca: 0.0005 - 0.0050%

Ca is an element useful for morphological control of sulfide-based inclusions and can optionally be added. To achieve this effect, the Ca content must be 0.0005% or more. Accordingly, in the case of adding Ca, the Ca content is 0.0005% or more. If the Ca content is more than 0.0050%, ductility is reduced due to an increase in the number of inclusions in the steel, resulting in reduced workability when bending a wide strip. Accordingly, in the case of adding Ca, the Ca content is 0.0050% or less, and preferably 0.0025% or less.

Mg: 0.0005 - 0.0100%

Mg is an element that forms an oxide stable at high temperature to effectively suppress the coarsening of former austenite grains and improve ductility. To achieve this effect, the Mg content must be 0.0005% or more. Accordingly, in the case of adding Mg, the Mg content is 0.0005% or more. When the Mg content is more than 0.0100%, ductility decreases due to an increase in the number of inclusions in the steel, as a result of which the workability when bending a wide strip decreases. Accordingly, in the case of adding Mg, the Mg content is 0.0100% or less, and preferably 0.0050% or less.

REM: 0.0005 - 0.0200%

REM (rare earth metal) promotes the formation of oxide and sulfide in steel and improves the properties of the material, as is the case with Ca. To achieve this effect, the REM content must be 0.0005% or more. Accordingly, in the case of adding rare earth metals, the content of rare earth metals is 0.0005% or more. If the REM content is more than 0.0200%, the effect is saturated. Accordingly, in the case of adding rare earth metals, the content of rare earth metals is 0.0200% or less, and preferably 0.0100% or less.

Microstructure

Volume fraction of martensite: 90% or more

In the present invention, the volume fraction of martensite at a depth of 1 mm from the surface of the wear-resistant steel sheet is 90% or more. If the volume fraction of martensite is less than 90%, the hardness of the matrix of the wear-resistant steel sheet is reduced, so that the abrasion resistance is deteriorated. Therefore, the volume fraction of martensite is 90% or more. Since the higher the volume fraction of martensite, the better, no upper limit of the volume fraction is set, and the volume fraction can be 100%. The volume fraction of martensite can be measured by the method described in the examples section.

If the volume fraction of martensite is 90% or more, the desired abrasion resistance can be achieved regardless of the residual microstructure. Therefore, the residual microstructure other than martensite is not limited and can be any microstructure. For example, the residual microstructure may be one or more selected from the group consisting of ferrite, pearlite, austenite and bainite.

Hardness

Brinell hardness: 500 - 650 HBW 10/3000

In addition to the above chemical composition, the wear-resistant steel sheet according to the present invention has a Brinell hardness of 500 to 650 HBW 10/3000 at a depth of 1 mm from the surface. The reasons for the limitation of surface hardness will be described below.

The abrasion resistance of steel sheet can be improved by increasing the hardness of the surface layer of the steel sheet. If the hardness at a depth of 1 mm from the surface of the steel sheet is less than 500 HBW Brinell, sufficient abrasion resistance cannot be achieved, resulting in a shortened service life. Accordingly, the Brinell hardness at a depth of 1 mm from the surface of the steel sheet is 500 HBW or more. If the hardness at a depth of 1 mm from the surface of the steel sheet is more than 650 HBW Brinell, the bending machinability of the wide strip is deteriorated. Accordingly, the Brinell hardness at a depth of 1 mm from the surface of the steel sheet is 650 HBW or less. The Brinell hardness here is the value (HBW 10/3000) measured at a position 1/4 of the sheet width using a 10 mm diameter hard tungsten ball with a load of 3000 kgf.

Difference in hardness in the transverse direction

Hardness difference in the transverse direction: 30Hv10 or less

If the wear-resistant steel sheet has a locally hardened zone or a softening zone, the deformation is concentrated around the softening zone or the hardening zone, and the ductility is reduced, so that suitable wide strip bending machinability cannot be achieved. In view of this, in the present invention, the hardness difference in the transverse direction is 30Hv10 or less on the Vickers scale. The hardness difference in the transverse direction in the description is defined as the difference in hardness at a depth of 1 mm from the surface of the wear-resistant steel sheet between two adjacent points at intervals of 10 mm in the transverse direction of the plate. As a result of the difference in hardness being within this range, bending workability is adequate even when bending a wide strip. Since a steel sheet is generally produced by moving in a rolling direction, if uniformity is maintained in the transverse direction (that is, in a direction orthogonal to the rolling direction), uniformity is equally maintained in the rolling direction.

The difference in hardness in the transverse direction can be assessed by measuring the Vickers hardness at a distance of 1 mm from the surface of the wear-resistant steel sheet at intervals of 10 mm between adjacent measurement points in the transverse direction and calculating the difference in hardness. The expression “the hardness difference in the transverse direction is 30Hv10 or less” means that the hardness difference between each pair of adjacent points is 30Hv10 or less, that is, the maximum hardness difference between two adjacent points is 30Hv10 or less.

To cut wear-resistant steel sheet, thermal cutting such as gas cutting, plasma cutting or laser cutting is usually used. In thermally cut wear-resistant steel sheet, the hardness at the edge portions changes due to the effect of heat during cutting. Therefore, the heat-affected zones on the edge parts of the wear-resistant steel sheet are excluded from the measurement of the hardness difference in the transverse direction. Specifically, Vickers hardness measurements are carried out at intervals of 10 mm in the transverse direction, except for an area of 50 mm from each edge of the wear-resistant steel sheet. In this way, the difference in hardness in the transverse direction can be determined.

If the measurement is carried out at intervals of more than 10 mm, it is not possible to detect the change in hardness that causes deterioration in bending workability. The shorter the intervals between measurement points, the higher the accuracy of determining the change in hardness, but the number of measurement points is huge. Moreover, it has been shown that appropriate performance can actually be achieved by controlling hardness differences measured at 10 mm intervals, as described in the examples section below. For these reasons, the measuring interval is 10 mm.

Sheet thickness

The thickness of the wear-resistant steel sheet according to the present invention is not limited and can be any thickness of the sheet. Considering that wear-resistant steel sheets with a thickness of 4 to 60 mm are especially necessary in order to have wide strip bending machinability, the thickness of the wear-resistant steel sheet is preferably 4 to 60 mm.

Preparation method

Below, a method for manufacturing a wear-resistant steel sheet according to one embodiment of the present invention will be described. The wear-resistant steel sheet according to the present invention can be manufactured by heating a steel material having the above chemical composition, hot rolling the steel material, and then subjecting the resulting steel sheet to heat treatment, including quenching under the conditions described below.

Steel material

Any form of material can be used as the steel material. For example, the steel material may be a steel slab.

The manufacturing method of the steel material is not limited. For example, steel material can be produced by melting steel having the above chemical composition in a conventional manner and casting steel. Melting can be done by any method such as in a converter, electric furnace or induction furnace. Casting is preferably carried out by continuous casting from the point of view of productivity, but casting into ingots can be carried out.

Heat

The steel material is heated to heating temperature before hot rolling. Heating may be carried out after cooling the steel material obtained by casting or the like. Alternatively, the resulting steel material can be directly heated without cooling.

Heating temperature: Ac3 transformation point or higher and 1300°C or lower.

If the heating temperature is below the Ac3 transformation point, then after heating the microstructure of the steel sheet contains a ferrite phase. In this case, not only sufficient hardness cannot be achieved after quenching, but also a uniform microstructure cannot be obtained. Therefore, the heating temperature corresponds to the Ac3 transformation point or higher. At heating temperatures above 1300°C, heating requires an excessive amount of energy, which causes a decrease in productivity. Therefore, the heating temperature is 1300°C or less, preferably 1250°C or less, more preferably 1200°C or less, and even more preferably 1150°C or less.

The Ac3 transformation point can be calculated using the following formula:

Ac3 (°C) = 912.0 - 230.5 × C + 31.6 × Si - 20.4 × Mn - 39.8 × Cu - 18.1 × Ni - 14.8 × Cr + 16.8 × Mo

where each element symbol in the formula represents the content of the corresponding element in % by weight, with the content of each element not contained being equal to 0.

Hot rolling

The heated steel material is then hot rolled to obtain a hot rolled steel sheet. The hot rolling conditions are not limited, and hot rolling can be carried out in a conventional manner. In the present invention, hardness, etc. The steel sheet is controlled during the heat treatment process after hot rolling, and accordingly, the hot rolling conditions are not limited. However, from the viewpoint of reducing the specific pressure of the steel material on the rolls and reducing the load on the rolling mill, the final rolling temperature is preferably 750°C or more, more preferably 800°C or more, and even more preferably 850°C or more. From the point of view of preventing significant coarsening of austenite grains and the associated reduction in ductility after heat treatment, the final rolling temperature is preferably 1000°C or less, or more preferably 950°C or less.

In the present invention, the hot-rolled steel sheet is subjected to heat treatment including quenching. The heat treatment can be carried out in any of the two embodiments described below. In the following description, the term “cooling start temperature” refers to the surface temperature of the steel sheet at the start of cooling in the quenching cooling process, and the term “cooling end temperature” refers to the surface temperature of the steel sheet at the end of cooling in the quenching cooling process.

In one embodiment of the present invention, after hot rolling, the resulting hot rolled steel sheet is subjected to quenching. Quenching is done by (a) direct quenching (DQ) or (b) reheat quenching (RQ). Although the cooling method for quenching is not limited, water cooling is preferred.

(a) Direct quench (DQ)

In the case of quenching by direct quenching, the hot-rolled steel sheet after hot rolling is cooled from a cooling start temperature equal to or more than the Ar3 transformation temperature to a cooling end temperature equal to or below the Mf point.

Cooling start temperature: Ar3 transformation point or more

If the cooling start temperature is equal to the Ar3 transformation temperature or higher, quenching starts from the austenitic region, so that the desired martensitic microstructure can be obtained. If the initial cooling temperature is below the Ar3 point, ferrite is formed, causing the volume fraction of martensite in the final microstructure to be less than 90%. If the volume fraction of martensite is less than 90%, the hardness of the steel sheet cannot be improved sufficiently, and therefore the abrasion resistance of the steel sheet is reduced. Moreover, if the initial cooling temperature is below the Ar3 point, a difference in hardness in the transverse direction occurs, so that the bending machinability of the wide strip is reduced. Although the upper limit of the cooling start temperature is not set, the cooling start temperature is preferably 950° C. or lower.

The Ar3 transformation point can be calculated using the following formula:

Ar3 (°C) = 910 - 273 × C - 74 × Mn - 57 × Ni - 16 × Cr - 9 × Mo - 5 × Cu

where each element symbol in the formula represents the content of the corresponding element in % by weight, with the content of each element not contained being equal to 0.

Cooling end temperature: Mf point or below

If the cooling end temperature is above the Mf point, the volume fraction of martensite cannot be increased sufficiently and the desired hardness cannot be achieved. Moreover, if the cooling end temperature is higher than the Mf point, a difference in hardness in the transverse direction occurs, so that the bending machinability of the wide strip is reduced. Therefore, the cooling end temperature is point Mf or lower. The cooling end temperature is preferably (point Mf - 100°C) or less, more preferably (point Mf - 120°C) or less, and even more preferably (point Mf - 150°C) or less, from the point of view of increasing the volume fraction of martensite . Although the lower limit of the cooling termination temperature is not set, the cooling termination temperature is preferably room temperature or higher since excessive cooling causes a decrease in manufacturing efficiency.

Point Mf can be calculated using the following formula:

Mf (°C) = 410.5 - 407.3 × C - 7.3 × Si - 37.8 × Mn - 20.5 × Cu - 19.5 × Ni - 19.8 × Cr - 4.5 × Mo

where each element symbol in the formula represents the content of the corresponding element in % by weight, with the content of each element not contained being equal to 0.

(b) Reheat Quenching (RQ)

In the case of reheat quenching, first the hot rolled steel sheet after hot rolling is cooled, and the hot rolled steel sheet after cooling is reheated to a reheat temperature equal to the Ac3 transformation point or higher and 950° C. or lower. The hot-rolled steel sheet, after being reheated, is then cooled from the reheating temperature to a cooling end temperature equal to or below the Mf point.

Reheat temperature: Ac3 transformation point or higher and 950°C or lower

Reheating the hot-rolled steel sheet to the Ac3 transformation point or above can make the microstructure austenitic, so that a martensitic microstructure can be obtained by subsequent quenching (cooling). If the reheating temperature is lower than the Ac3 transformation point, ferrite is formed and the steel sheet is not sufficiently hardened, and therefore the hardness of the steel sheet cannot be improved sufficiently. This causes a decrease in the abrasion resistance of the final steel sheet. Therefore, the reheat temperature is equal to the Ac3 transformation temperature or higher. If the initial reheat temperature exceeds 950°C, the crystal grains become larger and the workability decreases. Thus, the reheat temperature is 950°C or less. For example, to start cooling from the reheat temperature, cooling is started immediately after the hot-rolled steel sheet is discharged from the furnace used for reheating.

Cooling end temperature: Mf point or below

If the cooling end temperature is above the Mf point, the volume fraction of martensite cannot be increased sufficiently and the desired hardness cannot be achieved. Moreover, if the cooling stop temperature is higher than the Mf point, a difference in hardness in the transverse direction occurs, so that the bending machinability of the wide strip is reduced. Thus, the cooling end temperature is at or below the Mf point. The cooling end temperature is preferably (point Mf - 100°C) or less, more preferably (point Mf - 120°C) or less, and even more preferably (point Mf - 150°C) or less, from the point of view of increasing the volume fraction of martensite . Although the lower limit of the cooling termination temperature is not set, the cooling termination temperature is preferably room temperature or higher since excessive cooling causes a decrease in manufacturing efficiency.

Average cooling rate during quenching

The cooling rate during the quenching cooling process is not limited and can be any cooling rate at which a martensite phase is formed. For example, the average cooling rate from the start of quenching to the end of quenching is preferably 10°C/s or more, more preferably 15°C/s or more, and even more preferably 20°C/s or more. Since a higher average cooling rate during quenching is in principle better, no upper limit is set for the average cooling rate. However, given that a higher cooling rate requires a cooling line capable of cooling at a given cooling rate, the average cooling rate is preferably 150°C/s or less, more preferably 100°C/s or less, and even more preferably 80°C /s or less. The average cooling rate in the description means the average cooling rate of the surface temperature at the center position of the steel sheet in the transverse direction. Surface temperature can be measured using a radiation thermometer or similar device.

Difference in cooling rate

In the present invention, in the quenching cooling process, the difference in the average cooling rate between the center position and the 1/4 position in the transverse direction of the hot-rolled steel sheet and the difference in the average cooling rate between the center position and the 3/4 position in the transverse direction of the hot-rolled steel sheet is 5°C/s or less. If the difference in average cooling rate (hereinafter also called “difference in cooling rate”) is more than 5°C/s, the difference in Vickers hardness between two adjacent points is more than 30Hv10, and the bending workability of the wide strip is deteriorated. The average cooling rate in the description means the average rate of decrease in the surface temperature of the steel sheet. Surface temperature can be measured using a radiation thermometer or similar device.

Hardening

In one embodiment of the present invention, the hardened hot-rolled steel sheet may be further tempered. Tempering can further improve the uniformity of hardness of the steel sheet. In the case of tempering, the end temperature of cooling during quenching is preferably lower than (point Mf - 100°C). After cooling is completed at the cooling end temperature, the steel sheet is heated to the tempering temperature described below.

Temperature: (point Mf - 80°C) or higher and (point Mf + 50°C) or lower

If the tempering temperature is lower (point Mf - 80°C), the tempering effect cannot be achieved. Accordingly, in the case of tempering, the tempering temperature is (Mf point - 80°C) or more, preferably (Mf point - 60°C) or more, or more preferably (Mf point - 50°C) or more. At a tempering temperature above (point Mf + 50°C), the surface hardness decreases noticeably. Accordingly, in the case of tempering, the tempering temperature is (point Mf + 50°C) or less, preferably (point Mf + 30°C) or less, or more preferably (point Mf + 10°C) or less.

Holding temperature

Once the tempering temperature has been reached, heating can be stopped. However, in one embodiment of the present invention, after heating to the tempering temperature, the steel sheet may be maintained at the tempering temperature for any holding time. The holding time is not limited, but is preferably 60 seconds or more, or more preferably 5 minutes or more from the viewpoint of enhancing the tempering effect. If the holding time is excessively long, the hardness of the steel sheet may decrease. Accordingly, in the case of holding at a predetermined temperature, the holding time is preferably 60 minutes or less, more preferably 30 minutes or less, and even more preferably 20 minutes or less.

Heating rate

The rate of heating to the tempering temperature during tempering is not limited. The average heating rate to the tempering temperature is preferably 0.1°C/s or more, or more preferably 0.5°C/s or more from the point of view of productivity. If the average heating rate is 2°C/s or more, fine carbide is precipitated, which can further improve wide strip bending machinability. Therefore, the average heating rate is preferably 2°C/s or more, or more preferably 10°C/s or more from the viewpoint of further improving the bending processability of the wide strip. Although there is no upper limit to the average heating rate, excessively high heating rates require a larger reheat line and also result in increased energy consumption. Thus, the average heating rate is preferably 30°C/s or less, or more preferably 25°C/s or less.

Heating during tempering is not limited and can be carried out in any way. For example, at least one method selected from the group consisting of heating using a heat treatment furnace, high frequency induction heating, and electric heating may be used. In the case of holding at a given temperature, it is preferable to perform reheating and holding using a heat treatment oven. In the case where the average heating rate is 2°C/s or more, heating to the tempering temperature is preferably carried out by high-frequency induction heating or electric heating. In the case of using a heat treatment furnace, the average heating rate is preferably 10°C/s or less. Exposure can be performed either offline or online.

After heating to the tempering temperature and optionally holding at a given temperature, heating or holding is stopped. The subsequent cooling method is not limited, and may be air cooling and water cooling. In one embodiment of the present invention, after stopping heating or holding at a given temperature, the steel sheet can be left to naturally cool to room temperature.

In another embodiment of the present invention, the quenching cooling is stopped at a certain temperature range and then air cooling is performed. In this way, the steel sheet is subjected to tempering, so that the hardness uniformity of the steel sheet can be further improved as in the case of tempering in the previous embodiment. This implementation will be described below.

Cooling end temperature: Mf point or less and (Mf point - 100°C) or more

If the temperature at the end of cooling during quenching is above the Mf point, the volume fraction of martensite cannot be increased sufficiently and the desired hardness cannot be achieved, as indicated above. Moreover, if the cooling stop temperature is higher than the Mf point, a difference in hardness in the transverse direction occurs, so that the bending machinability of the wide strip is reduced. Therefore, the cooling end temperature is at or below the Mf point. If the cooling end temperature is less than (Mf point - 100°C), the tempering effect cannot be achieved even if air cooling is performed after cooling is completed. Therefore, in this embodiment, the cooling end temperature is (point Mf - 100°C) or more. The cooling termination temperature is preferably (Mf point - 80° C.) or higher, or more preferably (Mf point - 50° C.) or higher from the viewpoint of enhancing the air-cooling tempering effect.

In this embodiment, the tempering effect can be achieved by performing air cooling after finishing cooling at the cooling finishing temperature. Air cooling is not limited and can be carried out under any conditions, but the cooling rate is preferably 1°C/s or less.

Examples

To demonstrate the effects of the currently disclosed methods, wear-resistant steel plates were prepared using the procedure described below and their properties were evaluated.

First, molten steels having the chemical compositions listed in Table 1 are produced by smelting and steel slabs are prepared as steel materials. Each resulting steel slab is heated to the heating temperature specified in Table 2, and then subjected to hot rolling under the conditions specified in Table 2 to obtain a hot-rolled steel sheet. The resulting hot-rolled steel sheet is subjected to direct quenching or reheat quenching under the conditions shown in Table 2 to obtain a wear-resistant steel sheet. In some examples, after quenching, tempering is carried out under the conditions shown in Table 2. In each example without tempering, after quenching, air cooling is carried out at a cooling rate of 1°C/s or less.

The column "Difference in cooling rate" in Table 2 shows the larger value of the difference in the average cooling rate between the center position and the 1/4 position in the transverse direction of the hot-rolled steel sheet and the difference in the average cooling rate between the center position and the 3/4 position of the hot-rolled steel sheet. sheet in the transverse direction during the cooling process during quenching.

For each resulting wear-resistant steel sheet, the volume fraction of martensite (M), hardness, maximum hardness difference in the transverse direction and bending radius of the wide strip are assessed. The assessment methods are as follows.

Volume fraction of martensite

A sample is taken from each steel sheet so that a point at a depth of 1 mm from the surface of the steel sheet is the observation point. The surface of the sample is polished to a mirror finish and additionally etched with nital, and then an area measuring 10 mm × 10 mm is photographed using a scanning electron microscope (SEM). The resulting image is analyzed using an image analyzer to determine the area fraction of martensite. Ten observation fields are randomly observed and the average value of the resulting area fractions is taken as the volume fraction of martensite.

Surface hardness

A hardness sample is taken from each produced wear-resistant steel sheet and the Brinell hardness is measured in accordance with JIS Z 2243 (1998). To eliminate the influence of scale and the decarburized layer on the surface of a wear-resistant steel sheet, the measurement is carried out after removing a section from the surface of the steel sheet to a depth of 1 mm by grinding. Therefore, the measured hardness is the hardness of the plane at a depth of 1 mm from the surface of the steel sheet. The cross direction measuring point represents a position equal to 1/4 of the sheet width (ie, the 1/4 cross direction position). When measuring, a solid tungsten ball with a diameter of 10 mm and a load of 3000 kgf are used.

Difference in hardness in the transverse direction

The Vickers hardness at a depth of 1 mm from the surface of each wear-resistant steel sheet is measured at intervals of 10 mm in the transverse direction. When measuring, an area of 50 mm from each edge of the transverse direction of the wear-resistant steel sheet is excluded from the measurement range. Based on the obtained values, the absolute difference in Vickers hardness between two adjacent points is calculated. The maximum absolute difference value is shown in Table 3. The test load for Vickers hardness measurement is 10 kg.

Bend radius limitation

From each resulting steel sheet, a bending test sample of 200mm width and 300mm length is taken and a bending test is carried out with a bending angle of 180° in accordance with JIS Z 2248. From the minimum bending radius R (mm) without cracking and the thickness of the sheet t (mm) when testing for bending, the maximum bending radius R/t is calculated.

The evaluation results obtained by these methods are listed in Table 3. As can be understood from the results in Table 3, each wear-resistant steel sheet satisfying the conditions of the present invention has a Brinell surface hardness of 500 - 650 HBW 10/3000 and suitable abrasion resistance. Each wear-resistant steel sheet satisfying the conditions of the present disclosure also has a maximum bending radius R/t of 7.0 or less in the bending test, demonstrating suitable wide strip bending machinability. Thus, each wear-resistant steel sheet according to the present invention has suitable both abrasion resistance and wide strip bending workability. These results indicate that the methods disclosed in the present invention can improve the bending machinability of wide strip without reducing the surface hardness of the wear-resistant steel sheet.

Table 3

Claims (65)

1. Wear-resistant steel sheet having a chemical composition containing, in wt.%: C: more than 0.30 and 0.45 or less Si: 0.05 - 1.00 Mn: 0.50 - 2.00 P: 0.020 or less S: 0.010 or less Al: 0.01 - 0.06 Cr: 0.10 - 1.00 N: 0.0100 or less optionally at least one element selected from the group consisting of: Nb: 0.005 - 0.020 Ti: 0.005 - 0.020 and B: 0.0003 - 0.0030, optionally at least one element selected from the group consisting of: Cu: 0.01 - 0.5 Ni: 0.01 - 3.0 Mo: 0.1 - 1.0 V: 0.01 - 0.10 W: 0.01 - 0.5 and Co: 0.01 - 0.5, optionally at least one element selected from the group consisting of: Ca: 0.0005 - 0.0050 Mg: 0.0005 - 0.0100 and REM: 0.0005 - 0.0200 the rest is Fe and inevitable impurities, wherein the volume fraction of martensite at a depth of 1 mm from the surface of the wear-resistant steel sheet is 90% or more, Brinell hardness at a depth of 1 mm from the surface is 500 - 650 HBW 10/3000, and the Vickers hardness difference in the transverse direction is 30Hv10 or less, wherein said hardness difference in the transverse direction is defined as the difference in hardness at a depth of 1 mm from the surface between two adjacent points at an interval of 10 mm in the transverse direction of the wear-resistant steel sheet. 2. A method for manufacturing wear-resistant steel sheet, including: heating a steel material to a heating temperature that corresponds to the Ac3 transformation point or more and 1300°C or less, wherein the steel material has a chemical composition containing, in wt.%: C: more than 0.30 and 0.45 or less Si: 0.05 - 1.00 Mn: 0.50 - 2.00 P: 0.020 or less S: 0.010 or less Al: 0.01 - 0.06 Cr: 0.10 - 1.00 N: 0.0100 or less optionally at least one element selected from the group consisting of: Nb: 0.005 - 0.020 Ti: 0.005 - 0.020 and B: 0.0003 - 0.0030, optionally at least one element selected from the group consisting of: Cu: 0.01 - 0.5 Ni: 0.01 - 3.0 Mo: 0.1 - 1.0 V: 0.01 - 0.10 W: 0.01 - 0.5 and Co: 0.01 - 0.5, optionally at least one element selected from the group consisting of: Ca: 0.0005 - 0.0050 Mg: 0.0005 - 0.0100 and REM: 0.0005 - 0.0200 the rest is Fe and inevitable impurities, hot rolling the heated steel material to obtain a hot rolled steel sheet; And carrying out hardening of hot-rolled steel sheet, wherein the quenching is (a) direct quenching, which cools the hot-rolled steel sheet from an initial cooling temperature equal to or greater than the Ar3 transformation temperature to a final cooling temperature equal to or less than the Mf point, or (b) reheat quenching, at which cools the hot-rolled steel sheet, reheats the cooled hot-rolled steel sheet to a reheating temperature that is the transformation point of Ac3 or more and 950°C or less, and cools the reheated hot-rolled steel sheet from the reheating temperature to the cooling end temperature equal to the point Mf or less, and In the cooling process of quenching, the difference in the average cooling rate between the center position and the 1/4 position in the transverse direction of the hot-rolled steel sheet and the difference in the average cooling rate between the center position and the 3/4 position in the transverse direction of the hot-rolled steel sheet is each 5° C/s or less. 3. The method according to claim 2, in which the temperature at the end of cooling during quenching is less than (point Mf - 100°C), wherein the method includes, after quenching, tempering the hardened hot-rolled steel sheet at a tempering temperature that is (point Mf - 80°C) or more and (point Mf + 50°C) or less. 4. The method according to claim 3, wherein when tempering, the hardened hot-rolled steel sheet is kept at the tempering temperature for 60 seconds or more. 5. The method according to claim 3 or 4, in which the average heating rate during tempering is 2°C/s or more. 6. The method according to claim 2, in which the temperature of the end of cooling during quenching corresponds to the point Mf or less and the point (Mf - 100°C) or more, wherein the method includes, after hardening, air cooling of the hardened hot-rolled steel sheet.