STEEL SHEET FOR NITRIDING AND PRODUCTION METHOD THEREFOR

A steel sheet for nitriding has excellent formability and punchability. The steel sheet has a composition including, in percent by mass, 0.02% to 0.08% of C, 0.1% or less of Si, 0.2% to 1.8% of Mn, 0.05% or less of P, 0.02% or less of S, 0.01% to 0.06% of Al, 0.5% to 1.5% of Cr, 0.01% or less of N, and the balance being Fe and incidental impurities; and has a microstructure including ferrite as a main phase and pearlite and/or bainite as a secondary phase. The ferrite has a fraction of 70% or more in the entire microstructure and an average grain diameter of 5 to 25 gm. An average length of the major axis of cementite present in the secondary phase in a cross section in the rolling direction of the steel sheet is 3.0 μm or less.

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Description
TECHNICAL FIELD

This disclosure relates to a steel sheet for nitriding which is used by being subjected to nitriding treatment to improve durability and which is suitable as a material for machine parts, in particular, a steel sheet for nitriding having excellent formability and punchability before nitriding treatment, and a method of producing the same. Background

In machine parts used for automotive transmissions and the like, to improve fatigue strength and abrasion resistance, steel as a material is formed into a desired part shape and then often subjected to a surface-hardening treatment before use. Typical examples of such a surface-hardening treatment are carburizing treatment and nitriding treatment.

Carburizing treatment is the most common surface-hardening treatment. However, in carburizing treatment, usually, carbon is diffused and infiltrated (carburized) into the surface portion of steel at a temperature of the A3 transformation point or more, and then the steel is subjected to quenching. Consequently, under the influence of distortion caused by quenching from the high temperature, a decrease in shape accuracy of parts is unavoidable. Furthermore, in the as-quenched state after carburizing, the toughness of the steel is markedly decreased. Accordingly, after quenching, it is necessary to perform tempering to recover toughness and perform correction of the shape of parts. Therefore, when a carburizing treatment is employed, the number of processes required to manufacture parts increases, resulting in an increase in manufacturing costs, which is disadvantageous.

In contrast, in nitriding treatment, usually, steel is heated to a temperature of about 500° C. to 600° C. that is lower than the A1 transformation temperature so that nitrogen is diffused and infiltrated (nitrided) into the surface portion of steel, and the surface of steel is hardened without quenching, unlike the carburizing treatment. That is, in nitriding treatment, the treatment temperature is relatively low, and treatment is not accompanied by phase transformation of steel during cooling. Therefore, a decrease in shape accuracy of parts due to transformation strain does not occur, which is advantageous. Furthermore, the volume variation of the surface portion of steel due to nitriding is small, and it is easy to maintain good shape accuracy of parts, which is also advantageous.

In nitriding using ammonia gas, according to existing techniques, since the time required for nitriding is significantly long, the nitriding treatment is not suitable for automotive parts and the like that are supposed to be mass-produced. However, in recent years, a nitriding treatment referred to as nitrocarburizing in which a nitriding reaction is allowed to proceed rapidly by utilizing a carburizing atmosphere has become common. Thus, the significantly long treatment time, which is the problem in the existing techniques, is in the process of being solved.

In nitrocarburizing treatment, by holding an object to be treated in a treatment atmosphere at 550° C. to 600° C. for several hours, nitrogen is diffused and introduced into steel from the surface of steel by an iron carbide generating reaction. In accordance with the nitrocarburizing treatment, although the surface hardness obtained after the treatment is lower than that in the existing nitriding treatment, the time required for nitriding can be markedly reduced. For the reason described above, in recent years, the number of cases in which nitrocarburizing treatment is employed as the surface-hardening treatment, as an alternative to carburizing treatment, has been increasing.

On the other hand, according to existing techniques, machine parts used for automotive transmissions and the like are generally manufactured by subjecting intermediate products obtained by casting or forging to machining However, in recent years, thin steel sheets have been used as a material for machine parts, and machine parts have been manufactured by subjecting thin steel sheets to press working or the like to have a desired shape. The reason for this is that, by replacing parts manufactured by subjecting intermediate products obtained by casting or forging to machining in the existing techniques with sheet-metal working products of steel sheets, shortening of manufacturing processes and reduction in manufacturing costs can be achieved. Under such a background, there has been an increased demand for steel sheets for nitriding having excellent formability as a steel material for the machine parts.

Regarding a steel sheet for nitriding having excellent formability, various techniques have been proposed. For example, Japanese Unexamined Patent Application Publication No. 9-25513 and Japanese Unexamined Patent Application Publication No. 9-25543 propose techniques for producing a steel sheet for nitriding in which a steel having a composition including, in weight ratio, 0.01% to less than 0.08% of C, 0.005% to 1.00% of Si, 0.010% to 3.00% of Mn, 0.001% to 0.150% of P, 0.0002% to 0.0100% of N, more than 0.15% to 5.00% of Cr, more than 0.060% to 2.00% of Al, and one or two of Ti and V is hot-rolled, followed by coiling at 500° C. or higher, and then optionally subjected to cold rolling at a rolling reduction of 50% or more and subjected to perform recrystallization annealing. In accordance with those techniques, by producing a low-carbon steel sheet in which the content of C that adversely affects formability is suppressed to less than 0.08% and, at the same time, which contains Al, Cr, Ti and/or V which are nitriding accelerating elements, it is possible to obtain a steel sheet for nitriding having excellent formability and nitriding property.

Furthermore, Japanese Unexamined Patent Application Publication No. 2005-171331 proposes a technique on a steel sheet for nitrocarburizing in which the steel sheet has a composition including 0.01% to 0.10% by mass of C, 0.1% by mass or less of Si, 0.1% to 1.0% by mass of Mn, 0.05% by mass or less of P, 0.01% by mass or less of S, 0.01% to 0.06% by mass of Al, 0.05% to 0.50% by mass of Cr, 0.01% to 0.30% by mass of V, 0.01% by mass or less of N, and the balance being Fe and incidental impurities. In accordance with the technique proposed in Japanese Unexamined Patent Application Publication No. 2005-171331, it is possible to obtain a steel sheet for nitrocarburizing in which the production cost is low because of reduced amounts of alloy elements, which has excellent formability, and which can be used to produce a steel sheet having an excellent surface hardening property by nitrocarburizing treatment because of simultaneous addition of Cr and V which are nitriding accelerating elements.

When machine parts used for automotive transmissions and the like are manufactured by subjecting a thin steel sheet to forming, in many cases, the thin steel sheet is blanked to a predetermined size prior to forming, and holes with various shapes are pierced after forming. Accordingly, the steel sheet as the material for the parts is required to have excellent formability and excellent punchability. When the punchability of the steel sheet is degraded, occurrence of sags, burrs, and the like in punched surfaces during punching increases markedly, which impairs the dimensional accuracy of the machine parts. There may be cases where microcracks are likely to occur in punched surfaces, thus adversely affecting the strength property of the machine parts.

However, in the existing techniques described above, no consideration is given to punchability of the steel sheets. Furthermore, the problems described below remain.

In the techniques proposed in Japanese Unexamined Patent Application Publication No. 9-25513 and Japanese Unexamined Patent Application Publication No. 9-25543, the composition includes a large amount of Al as a nitriding accelerating element. Therefore, there is a concern that inner defects and surface defects resulting from Al-containing inclusions may occur, and generation of a large amount of Al-containing slag increases refining costs during smelting.

In accordance with the technique proposed in Japanese Unexamined Patent Application Publication No. 2005-171331, even if the amounts of alloy elements for nitriding acceleration are decreased, a sufficient hardening property can be imparted to a steel sheet for nitrocarburizing. However, the resulting steel sheet has insufficient strength, and it is difficult to apply the technique to heavily-loaded parts.

It could therefore be helpful to provide a steel sheet for nitriding which can be widely used as a material for parts such as automotive transmissions, and which has excellent formability and excellent punchability before nitriding treatment, and a method of producing the same.

SUMMARY

We found that by adjusting the chemical composition and microstructure of a steel sheet to certain ranges, a good hardening property can be provided by nitriding treatment, and it is possible to impart sufficient formability and punchability to a steel sheet before nitriding treatment.

We thus provide:

[1] A steel sheet for nitriding having a composition and microstructure; the composition including, in percent by mass, 0.02% to 0.08% of C, 0.1% or less of Si, 0.2% to 1.8% of Mn, 0.05% or less of P, 0.02% or less of S, 0.01% to 0.06% of Al, 0.5% to 1.5% of Cr, 0.01% or less of N, and the balance being Fe and incidental impurities, and the microstructure including ferrite as a main phase and pearlite and/or bainite as a secondary phase, wherein the ferrite has an area fraction of 70% or more in the entire microstructure and an average grain diameter of 5 to 25 μm, and cementite present in the secondary phase has an average length of the major axis of 3.0 μm or less in a cross section in the rolling direction of the steel sheet.

[2] The steel sheet for nitriding according to [1], wherein the composition further includes, in percent by mass, at least one selected from the group consisting of 0.005% to 0.075% of V, 0.005% to 0.025% of Nb, and 0.005% to 0.025% of Ti.

[3] A method of producing a steel sheet for nitriding including:

heating a steel slab having a composition including, in percent by mass, 0.02% to 0.08% of C, 0.1% or less of Si, 0.2% to 1.8% of Mn, 0.05% or less of P, 0.02% or less of S, 0.01% to 0.06% of Al, 0.5% to 1.5% of Cr, 0.01% or less of N, and the balance being Fe and incidental impurities, to 1,050° C. to 1,250° C.;

hot rolling the heated steel slab at a finishing temperature ranging from the Ar3 transformation temperature to (the Ar3 transformation temperature+100° C.);

cooling the hot rolled steel sheet at a cooling rate of 40° C./s to 80° C./s in the temperature range from the finishing temperature to 750° C. and at a cooling rate of 15° C./s to 35° C./s in the temperature range from 750° C. to a cooling stop temperature of 500° C. to 650° C.; and coiling the cooled steel sheet at a coiling temperature of 500° C. to 650° C.

[4] The method of producing a steel sheet for nitriding according to [3], wherein the composition of the steel slab further includes, in percent by mass, at least one selected from the group consisting of 0.005% to 0.075% of V, 0.005% to 0.025% of Nb, and 0.005% to 0.025% of Ti.

It is possible to obtain a steel sheet having excellent formability and punchability and a good hardening property by nitriding treatment. The steel sheet is very suitable as a material for formed parts to be subjected to nitriding treatment such as automotive transmission parts, thus exhibiting industrially marked effects. Furthermore, the steel sheet is not limited to being used for gas nitrocarburizing treatment and salt bath nitrocarburizing treatment, but can also be suitably used as any of various steel sheets for nitriding such as plasma nitriding, gas nitriding, carbonitriding, and nitrosulphurizing.

DETAILED DESCRIPTION

First, the microstructure of a steel sheet for nitriding will be described. The steel sheet has a microstructure including ferrite (which may also be referred to as “polygonal ferrite”), which is a main phase, and a secondary phase. The secondary phase includes pearlite and/or bainite. Furthermore, the fraction of the ferrite in the entire microstructure is 70% or more, the average grain diameter of the ferrite is 5 to 25 μm, and the average length of the major axis of cementite present in the secondary phase in a cross section in the rolling direction of the steel sheet is 3.0 μm or less.

Main Phase: Ferrite

In the steel sheet, by using soft ferrite as a main phase, formability of the steel sheet can be secured. When a material other than ferrite is used as the main phase, it is not possible to impart good formability to the steel sheet. However, in a steel sheet having a ferrite single-phase microstructure, it is not possible to secure sufficient strength as a steel sheet material that can be widely used for automotive transmission parts and the like. Therefore, the steel sheet has a microstructure including ferrite as the main phase, and the secondary phase described below.

Secondary Phase: Pearlite and/or Bainite

The secondary phase, which is the remainder other than ferrite, includes one or two selected from the group consisting of pearlite and bainite. The secondary phase in the steel sheet microstructure has a role in reinforcing the strength of the steel sheet having soft ferrite as the main phase. When reinforcement of a microstructure having martensite as the secondary phase is employed, martensite is softened by an increase in temperature during nitriding treatment, resulting in an increased variation in the strength of the steel sheet. Therefore, to stably maintain the strength of the steel sheet even after being subjected to nitriding treatment in which the steel sheet is held at about 500° C. to 600° C., the secondary phase in the steel sheet microstructure is required to be composed of pearlite and/or bainite.

Area Fraction of Ferrite in the Entire Microstructure: 70% or More

It is necessary to set the area fraction of the ferrite, which is the main phase, to be 70% or more to impart good formability to the steel sheet. When the area fraction of the ferrite is less than 70%, formability of the steel sheet is likely to be at an insufficient level. Furthermore, punchability of the steel sheet decreases. For example, during punching of the steel sheet, the sheared surface ratio of punched surfaces decreases. On the other hand, when the area fraction of the ferrite is excessively high, the strength of the steel sheet may not reach the necessary level. Therefore, the area fraction of the ferrite is preferably 97% or less, and more preferably 95% or less.

Average Grain Diameter of Ferrite: 5 to 25 μm

When the average grain diameter of the ferrite is more than 25 μm, the surface properties of the steel sheet may be degraded during forming, and the smoothness of punched surfaces may be degraded, resulting in degradation of punchability of the steel sheet. Furthermore, when the grain diameter of the ferrite becomes coarse, the number of grain boundaries decreases. Consequently, grain boundary diffusion of N during nitriding treatment is suppressed, and there is a concern that the time required for the nitriding treatment may be elongated. On the other hand, when the average grain diameter of the ferrite is less than 5 μm, the steel sheet hardens, and formability is likely to be degraded. Therefore, the average grain diameter of the ferrite is 5 to 25 μm, and preferably 5 to 15 μm.

Average Length of the Major Axis of Cementite Present in the Secondary Phase in a Cross Section in the Rolling Direction of the Steel Sheet: 3.0 μm or Less

When the average length of the major axis of cementite present in the secondary phase in a cross section in the rolling direction of the steel sheet exceeds 3.0 μm, the stress concentration ratio increases at the interface between the cementite and the ferrite during punching of the steel sheet, which makes it easy to cause microcracks, and the fracture surface ratio at punched surfaces increases. Thus, punchability of the steel sheet is degraded. Therefore, the average length of the major axis is 3.0 μm or less. However, when the cementite becomes extremely small, microcracks are likely to occur in punched surfaces of the steel sheet. Therefore, the average length of the major axis is preferably 1.0 μm or more.

Reasons for limiting the chemical composition of the steel sheet will be described below. Hereinafter, “%”, which is the unit of measure for the constituent element content, means “percent by mass” unless otherwise indicated.

C: 0.02% to 0.08%

C is an element having an effect of increasing the strength of steel through solid solution strengthening and formation of the secondary phase. When the C content is less than 0.02%, it is not possible to secure a sufficient strength of the steel sheet as a material for parts. On the other hand, when the C content is exceeded 0.08%, the strength of the steel sheet increases excessively, resulting in a decrease in formability. Furthermore, the fraction of the secondary phase increases, and it is difficult to obtain cementite having a desired form. Therefore, the C content is 0.02% to 0.08%, and preferably 0.04% to 0.06%.

Si: 0.1% or Less

Si is an element effective in deoxidizing steel, and also has an effect of strengthening steel by solid solution strengthening. The Si content is preferably 0.01% or more to obtain these effects. However, when the Si content exceeds 0.1%, hardly eliminable scale is generated during hot rolling, and surface properties of the steel sheet degrade markedly. Therefore, the Si content is 0.1% or less, and preferably 0.05% or less.

Mn: 0.2% to 1.8%

Mn is an element that strengthens steel by solid solution strengthening. Furthermore, Mn has an effect of fixing, as precipitates, S which is present as an impurity in the steel, thus reducing adverse effects caused by S. When the Mn content is less than 0.2%, the effects cannot be obtained sufficiently, and it is not possible to secure the required strength of the steel sheet. On the other hand, when the Mn content is more than 1.8%, the strength of the steel sheet increases excessively, and a band-like microstructure due to microsegregation is likely to be formed, resulting in degradation in formability and punchability of the steel sheet. Therefore, the Mn content is 0.2% to 1.8%, and preferably 0.2% to 1.2%.

P: 0.05% or Less

P is an element present as an impurity in the steel and, when the P content is large, formability and toughness of the steel sheet degrade. Therefore, the P content is 0.05% or less, and preferably 0.03% or less.

S: 0.02% or Less

S is also an element present as an impurity in the steel and, when the S content is large, formability and toughness of the steel sheet degrade. Therefore, the S content is 0.02% or less, and preferably 0.01% or less.

Al: 0.01% to 0.06%

Al is an element added for the purpose of deoxidizing steel. When the Al content in the steel is less than 0.01%, it is not possible to obtain a sufficient deoxidizing effect. On the other hand, when the Al content in the steel is more than 0.06%, the deoxidizing effect is saturated, and there is a possibility that inner defects and surface defects will increase due to an increase in inclusions in the steel. Therefore, the Al content is 0.01% to 0.06%, and preferably 0.02% to 0.05%.

Cr: 0.5% to 1.5%

Cr has an effect of increasing the hardness of the surface portion of the steel sheet by forming nitrides in the steel by nitriding treatment, and is an important alloy element. Cr also has an effect of refining cementite in the steel. In terms of sufficient exhibition of such effects, it is necessary to set the Cr content at 0.5% or more. However, when the Cr content exceeds 1.5%, the hardened portion of the outermost layer is significantly embrittled by nitriding treatment, and the depth of the hardened portion may be decreased in some cases. Therefore, the Cr content is 0.5% to 1.5%, and preferably 0.5% to 1.0%.

N: 0.01% or Less

N is an element present as an impurity in the steel. A large amount of N degrades formability of the steel sheet, and there is a possibility that N will combine with nitriding accelerating elements such as Cr, before nitriding treatment, thus degrading the hardening property due to nitriding. Therefore, the N content is 0.01% or less, and preferably 0.005% or less.

The steel sheet may contain, in addition to the composition described above, one or two or more selected from the group consisting of 0.005% to 0.075% of V, 0.005% to 0.025% of Nb, and 0.005% to 0.025% of Ti.

V: 0.005% to 0.075%

V is an element having an effect of increasing the hardness of the surface portion of the steel sheet by forming nitrides in the steel by nitriding treatment. Furthermore, since V is a carbide/nitride forming element, V also has an effect of increasing the strength of steel by particle dispersion strengthening (precipitation strengthening). Accordingly, V can be incorporated for the purpose of controlling the hardening property due to nitriding treatment and adjusting the level of strength of the steel sheet. In terms of sufficient exhibition of such effects, the V content is preferably 0.005% or more. On the other hand, when the V content is excessively large, formability is decreased by an excessive increase in the strength of the steel sheet, the hardened portion is embrittled by nitriding treatment, and also an economical disadvantage is caused. Therefore, the V content is preferably 0.005% to 0.075%, and more preferably 0.025% to 0.075%.

Nb: 0.005% to 0.025%

Nb is a carbide/nitride forming element having an effect of increasing the strength of steel by particle dispersion strengthening (precipitation strengthening). When the Nb content is less than 0.005%, such an effect cannot be sufficiently obtained. On the other hand, when the Nb content is more than 0.025%, there is a concern that the strength of the steel sheet will increase excessively, resulting in a decrease in formability. Therefore, the Nb content is preferably 0.005% to 0.025%, and more preferably 0.005% to 0.015%. Ti: 0.005% to 0.025%

Ti is also a carbide/nitride forming element having an effect of increasing the strength of steel by particle dispersion strengthening (precipitation strengthening). When the Ti content is less than 0.005%, such an effect cannot be sufficiently obtained. On the other hand, when the Ti content is more than 0.025%, there is a concern that the strength of the steel sheet may increase excessively, resulting in a decrease in formability. Therefore, the Ti content is preferably 0.005% to 0.025%, and more preferably 0.005% to 0.015%.

The balance other than the components described above includes Fe and incidental impurities. As the incidental impurities, 0.03% or less of Cu, 0.03% or less of Ni, 0.03% or less of Mo, 0.003% or less of Sn, 0.003% or less of Sb, 0.005% or less of 0, and the like are permissible.

A method of producing a steel sheet for nitriding will be described below.

A steel sheet can be obtained by heating, hot rolling, cooling, and coiling steel having the chemical composition described above.

The steel can be refined by any of known refining processes such as a converter process or an electric furnace process. The refined steel is formed into a steel (slab) by continuous casting or ingot casting and bloom rolling or the like. As necessary, preliminary treatments, secondary smelting, cleaning of the steel surface can be performed.

Heating Temperature of Steel: 1,050° C. to 1,250° C.

When the heating temperature of the steel is lower than 1,050° C., it is difficult to secure a desired finishing temperature during hot rolling. On the other hand, when the heating temperature of the steel exceeds 1,250° C., energy required for heating increases and defects in the surface properties of the steel sheet are likely to occur. Therefore, the heating temperature of the steel before hot rolling is 1,050° C. to 1,250° C., and preferably 1,100° C. to 1,200° C.

When the steel is heated, the steel cooled to normal temperature may be reheated, or the steel being cooled after casting may be subjected to additional heating or heat-retained.

After the steel is heated to the temperature range described above, rough rolling and finish rolling (hot rolling) are performed. The rough rolling may be performed under ordinary conditions, and rough rolling conditions are not particularly limited.

Finishing Temperature: Ar3 Transformation Temperature to (the Ar3 Transformation Temperature+100° C.)

When the finishing temperature in the hot rolling step is lower than the Ar3 transformation temperature, an un-recrystallized ferrite microstructure which is elongated in the rolling direction and a pancake-shaped, coarse ferrite microstructure are formed, and it is not possible to obtain ferrite with a desired grain diameter. Furthermore, formability and punchability of the steel sheet are degraded. Moreover, the in-plane anisotropy of mechanical properties of the steel sheet is increased. On the other hand, when the finishing temperature exceeds (the Ar3 transformation temperature+100° C.), surface properties of the steel sheet are likely to be degraded, the ferrite microstructure is likely to be coarsened, and it is difficult to obtain ferrite with a desired grain diameter. Therefore, the finishing temperature is the Ar3 transformation temperature to (the Ar3 transformation temperature+100° C.), and preferably (the Ar3 transformation temperature+20° C.) to (the Ar3 transformation temperature+100° C.). The steel sheet under rolling may be subjected to additional heating using a heating device such as a sheet bar heater or an edge heater to secure a necessary finishing temperature.

Cooling Rate from Finishing Temperature to 750° C.: 40° C./s to 80° C./s

The steel sheet which has been subjected to hot rolling is cooled (forced cooled) in the temperature range from the finishing temperature to 750° C. at a cooling rate of 40° C./s to 80° C./s, and preferably 45° C./s to 75° C./s. When the cooling rate in the temperature range is less than 40° C./s, the microstructure of the hot-rolled steel sheet is likely to be coarsened, and it is not possible to obtain ferrite or cementite having a desired shape. On the other hand, when the cooling rate in the temperature range is more than 80° C./s, martensite or excessively large amounts of bainite and pearlite are likely to be generated in the hot-rolled steel sheet, and it is difficult to obtain ferrite with a desired fraction or a desired secondary phase.

Cooling Rate from 750° C. to Cooling Stop Temperature: 15° C./s to 35° C./s

Cooling Stop Temperature: 500° C. to 650° C.

In the temperature range from 750° C. to a cooling stop temperature, cooling (forced cooling) is performed at a cooling rate of 15° C./s to 35° C./s, and preferably 15° C./s to 25° C./s. When the cooling rate in the temperature range is less than 15° C./s, the microstructure of the hot-rolled steel sheet is likely to be coarsened, and it is difficult to obtain ferrite or cementite having a desired shape. On the other hand, when the cooling rate in the temperature range is more than 35° C./s, progression of ferrite transformation is suppressed and it is not possible to obtain ferrite with a desired fraction.

When the cooling stop temperature is lower than 500° C., the steel sheet is hardened because martensite and an excessively large amount of bainite are generated. As a result, formability of the steel sheet is degraded and the strength of the steel sheet after nitriding treatment becomes unstable. On the other hand, when the cooling stop temperature is higher than 650° C., pearlite is coarsened, and it is not possible to obtain cementite having a desired shape. Therefore, the cooling stop temperature is 500° C. to 650° C., and preferably 500° C. to 600° C.

The steel sheet cooled to the cooling stop temperature may be directly coiled, or may be allowed to cool for a short period of time until it is coiled with a coiler. The term “being allowed to cool” refers to air cooling in the air in which forced cooling by pouring water is not performed. However, to remove cooling water remaining on the steel sheet, it is permissible to spray high-pressure water or compressed air for a very short period of time onto the steel sheet which is being allowed to cool because a decrease in the temperature of the steel sheet due to this is very small.

Coiling Temperature: 500° C. to 650° C.

When the coiling temperature is lower than 500° C., the steel sheet is hardened because martensite and an excessively large amount of bainite are generated. As a result, formability of the steel sheet is degraded and the strength of the steel sheet after nitriding treatment becomes unstable. On the other hand, when the coiling temperature is higher than 650° C., pearlite is coarsened, and it is not possible to obtain cementite having a desired shape. Therefore, the coiling temperature is 500° C. to 650° C., and preferably 500° C. to 600° C.

The coiled steel sheet is used after scale is removed by pickling or shot peening. Furthermore, the steel sheet may be subjected to temper rolling for the purpose of shape straightening and adjusting surface roughness. Performing such descaling or temper rolling does not impair the advantages.

EXAMPLES

Steels A to L containing constituent elements shown in Table 1 and the balance being Fe and incidental impurities were prepared in molten state. The resulting slabs were subjected to hot rolling under the conditions shown in Table 2, and thus hot-rolled steel sheets with a thickness of 2.3 mm were formed. Subsequently, the resulting hot-rolled steel sheets were descaled by pickling, and then subjected to temper rolling with an elongation of 0.5%. Specimens were taken from the hot-rolled steel sheets after temper rolling, and microstructure observation, a tensile test, and a punching test were performed. Furthermore, the hot-rolled steel sheets after temper rolling was subjected to nitriding treatment, and a hardness test was performed on the hot-rolled steel sheets after the nitriding treatment.

(1) Microstructure Observation

A specimen of a cross section in the thickness direction parallel to the rolling direction at the 1/4 width position was taken from each of the steel sheets before the nitriding treatment, and the specimen was subjected to mirror polishing and etched with nital. Using an image obtained by photographing the ¼ thickness position at an appropriate magnification of 500 to 5,000 times with an optical microscope or a scanning electron microscope, the microstructure was confirmed.

Regarding the fraction of ferrite in the microstructure, using the image described above, the area ratio of ferrite was obtained by image analysis, which was defined as the fraction of ferrite.

Regarding the average grain diameter of ferrite, using the image described above, grain diameters were determined in accordance with the method stipulated in Japan Industrial Standard JIS G 0551-2005, and the average grain diameter was calculated from the grain size number.

Regarding the average length of the major axis of cementite present in the secondary phase (pearlite and/or bainite), using the image described above, the length of the major axis of each of grains of cementite in the observation range was obtained, and the average was calculated by arithmetic average. These results are also shown in Table 2.

(2) Tensile Test (Evaluation of Formability)

Formability of the steel sheet was evaluated on the basis of ductility determined by a tensile test. The tensile test was carried out in accordance with JIS Z 2241-2011 using a No. 5 test specimen stipulated in JIS Z 2241-2011 which was taken at the ¼ width position of a steel sheet such that the testing direction corresponded to the rolling direction. Tensile strength (TS) and elongation after fracture (EL) were measured, and a strength-elongation balance (TS×EL) was calculated. The steel sheet having a strength-elongation balance value of 16 GPa·% or more was evaluated as having good formability.

(3) Punching Test (Evaluation of Punchability)

A disk-shaped test specimen with a diameter of 50 mm was punched out from a steel sheet before nitriding treatment (clearance: 5% of steel sheet thickness), the sheared surface ratio at the punched surface of the test specimen was measured, and presence or absence of microcracks in the fracture surface region was confirmed. When the sheared surface ratio was 60% or more, and no cracks were observed in the fracture surface region, the steel sheet was evaluated as having good punchability.

(4) Hardness Test (Evaluation of Surface Hardening Property Due to Nitriding Treatment)

A hot-rolled steel sheet after temper rolling was subjected to gas nitrocarburizing treatment, and the cross section hardness of the steel sheet after the gas nitrocarburizing treatment (nitrided layer cross section hardness) was measured. Gas obtained by mixing ammonia (NH3) and endothermic converted gas at the equal volume ratio was used as nitriding gas. The gas nitrocarburizing treatment temperature was 570° C., and the holding time at the gas nitrocarburizing treatment temperature was 150 minutes. After holding, oil cooling was performed. Regarding the cross section hardness of the steel sheet, a specimen of a cross section in the thickness direction parallel to the rolling direction was taken from the steel sheet after the gas nitrocarburizing treatment, and the Vickers hardness (HV0.1) at a depth of 0.2 mm from the surface of the steel sheet was measured in accordance with JIS Z 2244-2009. When the measured Vickers hardness was 250 or more, the surface hardening property of the steel sheet by nitriding treatment was evaluated to be good.

The results thereof are shown in Table 3.

TABLE 1 Chemical composition (mass %) Steel C Si Mn P S Al Cr N V Nb Ti A 0.02 0.08 1.8 0.02 0.007 0.02 1.5 0.003 — — — B 0.04 0.05 0.3 0.02 0.010 0.05 0.9 0.002 — — — C 0.04 0.03 0.2 0.02 0.005 0.04 0.8 0.002 0.005 — — D 0.05 0.03 0.6 0.03 0.005 0.06 1.0 0.002 — — — E 0.05 0.03 0.8 0.05 0.005 0.03 1.0 0.002 — 0.005 0.008 F 0.06 0.04 1.2 0.02 0.005 0.04 0.7 0.002 — — — G 0.06 0.02 1.0 0.01 0.005 0.05 0.8 0.001 0.065 — — H 0.06 0.05 1.2 0.03 0.005 0.05 0.6 0.001 0.050 0.008 — I 0.08 0.06 1.4 0.01 0.020 0.03 1.2 0.005 — — — J 0.05 0.03 0.7 0.04 0.005 0.04 0.4 0.002 — — — K 0.05 0.03 0.7 0.04 0.005 0.05 1.6 0.002 — — — L 0.12 0.03 1.2 0.02 0.005 0.03 0.6 0.002 — — —

TABLE 2 Hot rolling conditions Steel sheet microstructure *3 Ar3 Cooling Cooling F average C average Steel trans- Heating Finishing rate rate Cooling stop Coiling F grain length sheet formation temperature temperature 1 *1 2 *2 temperature temperature fraction diameter of major No. Steel point (° C.) (° C.) (° C.) (° C.) (° C.) (° C.) (° C.) Type (%) (μm) axis (μm)  1 A 761 1100 860 70 15 650 650 F, P 95 18 3.0  2 A 761 1250 920 70 15 650 650 F, P 95 28 3.5  3 A 761 1100 860 70 10 650 650 F, P 96 27 3.2  4 A 761 1100 860 60 15 690 680 F, P 96 29 3.8  5 B 812 1150 900 75 20 600 600 F, P 92 12 2.6  6 B 812 1000 760 40 20 610 600 F, P 94 26 2.8  7 C 811 1150 900 65 25 600 600 F, P 94 11 2.5  8 C 811 1150 900 35 20 610 600 F, P 93 16 3.1  9 D 807 1250 840 40 30 560 550 F, P 90  9 2.0 10 D 807 1250 840 80 45 550 540 F, P 68  8 1.6 11 E 806 1250 840 45 30 550 550 F, P 89  7 1.9 12 F 773 1200 860 60 25 580 580 F, P 82  7 1.7 13 F 773 1200 860 100  35 550 540 F, P, B 66  5 1.3 14 G 781 1200 860 60 25 590 580 F, P 78  7 1.5 15 G 781 1200 860 60 35 470 460 F, B, M 62  7 1.2 16 H 791 1200 860 55 25 550 540 F, P 74  6 1.4 17 I 744 1050 820 70 35 500 500 F, B 70  5 1.0 18 I 744 1050 840 65 25 520 520 F, P, B 72  6 1.2 19 J 810 1250 840 45 30 550 550 F, P 89 10 2.4 20 K 800 1250 840 45 30 550 550 F, P 91  8 1.6 21 L 749 1050 840 45 30 560 550 F, P 80  6 3.3 *1) Average cooling rate in the temperature range from the finishing temperature to 750° C. *2) Average cooling rate in the temperature range from 750° C. to the cooling stop temperature *3) F: ferrite, P: pearlite, B: bainite, M: martensite, C: cementite present in pearlite and/or bainite

TABLE 3 Formability Strength- Hardening Elongation elongation Punchability property Tensile after balance Sheared Nitrided layer Steel strength fracture TS × EL surface Cracks in cross section sheet TS EL (GPa · Eval- ratio fracture Eval- hardness Eval- No. Steel (MPa) (%) %) uation *4 (%) surface uation *4 HV0.1 (HV0.1) uation *4 Remarks  1 A 384 43.3 16.6 ◯ 68 Absent ◯ 262 ◯ Example of invention  2 A 371 41.8 15.5 X 63 Present X 249 X Comparative example  3 A 377 42.9 16.2 ◯ 64 Present X 256 ◯ Comparative example  4 A 369 43.1 15.9 X 65 Present X 243 X Comparative example  5 B 358 46.2 16.5 ◯ 65 Absent ◯ 285 ◯ Example of invention  6 B 345 39.7 13.7 X 48 Present X 278 ◯ Comparative example  7 C 362 45.6 16.5 ◯ 63 Absent ◯ 281 ◯ Example of invention  8 C 356 46.3 16.5 ◯ 61 Present X 273 ◯ Comparative example  9 D 379 43.9 16.6 ◯ 64 Absent ◯ 275 ◯ Example of invention 10 D 394 41.6 16.4 ◯ 58 Absent X 277 ◯ Comparative example 11 E 411 40.7 16.7 ◯ 66 Absent ◯ 287 ◯ Example of invention 12 F 409 42.8 17.5 ◯ 61 Absent ◯ 276 ◯ Example of invention 13 F 440 40.6 17.9 ◯ 56 Absent X 280 ◯ Comparative example 14 G 458 40.2 18.4 ◯ 62 Absent ◯ 319 ◯ Example of invention 15 G 522 34.7 18.1 ◯ 55 Present X 328 ◯ Comparative example 16 H 531 34.5 18.3 ◯ 60 Absent ◯ 337 ◯ Example of invention 17 I 603 27.6 16.6 ◯ 62 Absent ◯ 274 ◯ Example of invention 18 I 598 27.9 16.7 ◯ 63 Absent ◯ 271 ◯ Example of invention 19 J 371 44.4 16.5 ◯ 59 Absent X 171 X Comparative example 20 K 395 43.0 17.0 ◯ 65 Absent ◯ 222 X Comparative example 21 L 587 27.5 16.1 ◯ 60 Present X 269 ◯ Comparative example *4) ◯: Good, X: Poor

Our steel sheets (examples) have good formability, excellent punchability of the steel sheet, and an excellent surface hardening property due to nitriding treatment. On the other hand, in other steel sheets outside of our ranges in terms of the chemical composition and microstructure (comparative examples), any of or all of the formability, punchability, and surface hardening property due to nitriding treatment are at insufficient levels.

This application claims the benefit of Japanese Patent Application No. 2013-076824, filed Apr. 2, 2013, which is hereby incorporated by reference herein in its entirety.

Claims

1.-4. (canceled)

5. A steel sheet for nitriding having a composition and a microstructure:

the composition comprising in percent by mass,
0.02% to 0.08% of C, 0.1% or less of Si;
0.2% to 1.8% of Mn, 0.05% or less of P;
0.02% or less of S, 0.01% to 0.06% of Al;
0.5% to 1.5% of Cr, 0.01% or less of N; and
the balance being Fe and incidental impurities; and
a microstructure including ferrite as a main phase and pearlite and/or bainite as a secondary phase,
wherein the ferrite has a fraction of 70% or more in the entire microstructure and an average grain diameter of 5 to 25 μm, and cementite present in the secondary phase has an average length of a major axis of 3.0 μm or less in a cross section in a rolling direction of the steel sheet.

6. The steel sheet for nitriding according to claim 5, wherein the composition further comprises, in percent by mass, at least one selected from the group consisting of 0.005% to 0.075% of V, 0.005% to 0.025% of Nb, and 0.005% to 0.025% of Ti.

7. A method of producing a steel sheet for nitriding, comprising:

heating a steel slab having a composition including, in percent by mass, 0.02% to 0.08% of C, 0.1% or less of Si, 0.2% to 1.8% of Mn, 0.05% or less of P, 0.02% or less of S, 0.01% to 0.06% of Al, 0.5% to 1.5% of Cr, 0.01% or less of N, and the balance being Fe and incidental impurities, to 1,050° C. to 1,250° C.;
hot rolling the heated steel slab at a finishing temperature ranging from the Ar3 transformation temperature to (the Ar3 transformation temperature+100° C.);
cooling the hot rolled steel sheet at a cooling rate of 40° C./s to 80° C./s in the temperature range from the finishing temperature to 750° C. at a cooling rate of 15° C./s to 35° C./s in the temperature range from 750° C. to a cooling stop temperature of 500° C. to 650° C.; and
coiling the cooled steel sheet at a coiling temperature of 500° C. to 650° C.

8. The method according to claim 7, wherein the composition of the steel slab further includes, in percent by mass, at least one selected from the group consisting of 0.005% to 0.075% of V, 0.005% to 0.025% of Nb, and 0.005% to 0.025% of Ti.

9. The method according to claim 7, wherein the steel sheet has a microstructure including ferrite as a main phase and pearlite and/or bainite as a secondary phase, wherein the ferrite has a fraction of 70% or more in the entire microstructure and an average grain diameter of 5 to 25 μm, and cementite present in the secondary phase has an average length of a major axis of 3.0 μm or less in a cross section in a rolling direction of the steel sheet.

Patent History
Publication number: 20160032431
Type: Application
Filed: Mar 20, 2014
Publication Date: Feb 4, 2016
Inventors: Takashi Kobayashi (Tokyo), Hayato Saito (Tokyo), Yoshimasa Funakawa (Tokyo)
Application Number: 14/781,440
Classifications
International Classification: C22C 38/38 (20060101); C21D 9/46 (20060101); C21D 6/00 (20060101); C22C 38/28 (20060101); C22C 38/00 (20060101); C22C 38/24 (20060101); C22C 38/06 (20060101); C22C 38/04 (20060101); C22C 38/02 (20060101); C21D 8/02 (20060101); C22C 38/26 (20060101);