Patent Grant
12134812
This is a National Phase Application filed under 35 U.S.C. § 371, of International Application No. PCT/JP2019/021698, filed May 31, 2019, the contents of which are incorporated by reference.
The present disclosure and the claimed invention was made by, or on behalf of, parties to a joint research agreement. The joint research agreement was in effect on or before the effective filing date of the present disclosure and the claimed invention, and the present disclosure and the claimed invention was made as a result of activities undertaken within the scope of the joint research agreement. The parties to the joint research agreement are 1) NIPPON STEEL CORPORATION and 2) ISUZU MOTORS LIMITED.
The present disclosure relates to a steel material used for a steel piston.
An engine as typified by a diesel engine or the like includes a piston. The piston is housed inside a cylinder of the engine, and performs a reciprocating motion inside the cylinder. The piston is exposed to heat of a high temperature in a combustion process during operation of the engine.
Most conventional pistons are produced by casting aluminum. However, in recent years there is a demand to further improve the combustion efficiency of engines. In the case of a piston, which is an aluminum casting product, the surface temperature of the piston during use is within the range of around 240 to 330° C.
Recently, the use of pistons in even higher combustion temperatures ranges to increase the combustion efficiency is being studied. Therefore, there is a need for a material for a piston that can endure a situation in which the surface temperature of the piston becomes 400° C. or more, and even 500° C. or more during use. To address such needs, steel pistons that are produced using a steel material have started to be proposed. For example, a steel piston is proposed in Patent Literature 1. In comparison to a piston that is an aluminum casting product, the melting point of the starting material of a steel piston is high. Therefore, a steel piston can be used in a higher combustion temperature range in comparison to a piston that is an aluminum casting product.
In Patent Literature 2, technology that increases the lifetime of a steel piston is proposed. Specifically, in Patent Literature 2, the following matters are pointed out with regard to the lifetime of a steel piston. During use of a steel piston in a high combustion temperature region, oxide scale forms on the piston crown surface of the steel piston. When the oxide scale formed peels off from the piston crown, a scale notch is formed in the piston crown. As a result of the scale notch (region from which the oxide scale peeled off) widening, a crack occurs in the piston crown of the steel piston. To solve this problem, the technology disclosed in Patent Literature 2 forms a protective layer for suppressing the formation of oxide scale on the piston crown of a steel piston.
According to the aforementioned Patent Literature 2, the lifetime of a steel piston is increased by forming a protective layer on the steel piston. However, no particular consideration is given to the steel material to be used for the steel piston. In addition, in other literature also, no proposals have been made with regard to a steel material that is made suitable for a steel piston by adjusting the properties of the steel material itself.
An objective of the present disclosure is to provide a steel material for a steel piston that is suitable for use in a steel piston in which the surface temperature becomes 400° C. or more. More specifically, an objective is to provide a steel material for a steel piston that is (1) excellent in machinability during production of the steel piston, (2) excellent in high temperature fatigue strength and toughness during use of the steel piston, and (3) excellent in high temperature fatigue strength at a weld heat-affected zone (HAZ) in a case where the steel piston is produced by joining.
A steel material for a steel piston according to the present disclosure has a chemical composition which consists of, in mass %:
The steel material for a steel piston according to the present disclosure is suitable for use in a steel piston in which the surface temperature becomes 400° ° C. or more. More specifically, the steel material for a steel piston according to the present disclosure is (1) excellent in machinability during production of a steel piston, (2) excellent in high temperature fatigue strength and toughness during use of the steel piston, and (3) excellent in high temperature fatigue strength at a weld heat-affected zone (HAZ) in a case where the steel piston is produced by joining.
Initially, the present inventor conducted studies regarding the mechanical properties required for a steel material for a steel piston.
In the conventional research, for example, as described in Patent Literature 2, in general the following factor has been described as the principal reason why the lifetime of a steel piston decreases.
In a case where a steel piston is utilized in an engine for the purpose of increasing the combustion efficiency, the combustion temperature can be increased. Specifically, the surface temperature of a conventional piston is in the range of around 240 to 330° ° C. However, when a steel piston is utilized, the surface temperature of the piston can be increased by around 100° C. compared to the conventional piston. Specifically, in the case of a steel piston, even when the surface temperature of the piston is 400° C. or more, or 500° ° C. or more, it is possible for the steel piston to endure such a high temperature.
In a case where a steel piston is utilized, during operation of the engine, one part of the surface of a piston crown of the steel piston oxidizes and oxide scale forms. The adhesion of oxide scale with respect to a steel piston is low. Therefore, accompanying vertical motion of the steel piston, the oxide scale peels off from the steel piston. On the surface of the steel piston, the region from which oxide scale peels off is expanded as the time period for which the steel piston is used increases. Subsequently, a crack occurs in the region from which the oxide scale peeled off. The lifetime of a steel piston is determined by the above mechanism.
As described above, in the conventional research relating to steel pistons, it has been considered that the primary reason why the lifetime of a piston decreases is that oxide scale forms during operation of the engine.
However, the present inventors considered that the primary reason why the lifetime of a steel piston decreases is not oxide scale, but that the decrease is attributable to the following mechanism.
As described above, in an engine that uses a steel piston, in order to increase the combustion efficiency, the combustion temperature is a higher temperature (500° C. or more) than in the case of an engine that uses a conventional piston. Therefore, in an engine operating state, the steel piston is subjected to thermal expansion due to the combustion temperature. As a result, compressive stress arises in the steel piston in an engine operating state. On the other hand, when the engine enters a stopped state from an operating state, the engine is cooled to normal temperature. At such time, the steel piston contracts due to the cooling. Consequently, tensile stress arises in the steel piston when the engine is in a stopped state.
As described above, a steel piston inside an engine is subjected to compressive stress in a state in which the engine is operating and is subjected to tensile stress in a state in which the engine is stopped. An engine repeatedly switches between an operating state and a stopped state. In other words, when an operating state and a stopped state of an engine are repeated, the steel piston is repeatedly subjected to compressive stress and tensile stress alternately. Therefore, the present inventors considered that the primary factor that determines the lifetime of a steel piston is not the occurrence of cracking attributable to oxide scale which had heretofore being considered the primary factor, but that the primary factor is the occurrence of cracking due to thermal fatigue accompanying repeated switching between an operating state and a stopped state of the engine.
Therefore, the present inventors conducted studies regarding a method for suppressing a reduction in lifetime that is caused by thermal fatigue of a steel piston. In order to suppress the occurrence of a reduction in lifetime caused by thermal fatigue, the present inventors considered that it is effective to increase the fatigue strength within a temperature range of 500 to 600° C. that is the usage environment of a steel piston. In order to increase the fatigue strength, it is effective to increase strength of a steel material in a high temperature. If the strength at a high temperature can be increased, the occurrence of cracks or the like caused by thermal fatigue will be suppressed. As a result, the lifetime of a steel piston will be improved.
In general, the strength of a steel material decreases as the temperature increases. Therefore, if the strength at a normal temperature of the steel material is increased, although the strength will decrease accompanying a rise in temperature, the strength can be maintained to a certain extent even in a high-temperature region in which the surface temperature of the steel material becomes around 400 to 600° C.
However, a steel piston is produced by producing an intermediate product having a rough shape by performing hot forging of a steel material, and thereafter performing a cutting process. Consequently, if the strength at normal temperature of the steel material for the steel piston is high, the cutting process after producing the intermediate product will be difficult. Therefore, a steel material for a steel piston is required to have machinability prior to being used as a steel piston, and it is necessary for the steel material to have high fatigue strength at a high temperature during use as a steel piston. In addition, high toughness is also required during use as a steel piston. When considering the relation between temperature and toughness, the lower that the temperature is, the lower the toughness will be. Therefore, if the toughness at a normal temperature of a steel piston is sufficiently increased, the toughness in the range of 400 to 600° ° C. will also naturally increase.
Therefore, the present inventors conducted studies regarding a steel material that is excellent in machinability during production of a steel piston, and is also excellent in high temperature fatigue strength and excellent in toughness during use of the steel piston.
As described above, when the engine is in an operating state, a steel piston is exposed to a high-temperature region in which the surface temperature of the steel piston is 400° C. or more for an extended time period. Therefore, prior to being used as a steel piston, the strength of the steel material is kept low to maintain machinability. Subsequently, during use of the steel piston (during operation of the engine) in a high-temperature environment in which the surface temperature of the steel piston becomes 400 to 600° C., the high temperature strength of the steel material is increased by aging precipitation. In this case, while maintaining the machinability of the steel material, it is possible to increase the high temperature fatigue strength in a high-temperature region during operation of the engine.
In addition, in the process for producing a steel piston, in some cases the steel piston is formed by friction joining or laser joining of an upper member (upper part of the piston head) of the steel piston and a lower member (lower part of the piston head) of the steel piston. In a case where the aforementioned members are joined by one of these joining methods, a weld heat-affected zone (HAZ) that is affected by heat during joining is formed in a region in the vicinity of the joining interface. Therefore, it is necessary to secure the high temperature fatigue strength of a HAZ during use of the steel piston.
As described above, the present inventors considered that in the case of a steel material for a steel piston, it is necessary to (1) have excellent machinability during production of the steel piston, (2) have excellent high temperature fatigue strength and excellent toughness during use of the steel piston, and (3) secure the high temperature fatigue strength of a HAZ in a case where the steel piston is produced by joining. Therefore, the present inventors conducted studies regarding the chemical composition and structure of a steel material that satisfies the characteristics described in the foregoing (1) to (3). As a result, the present inventors obtained the following findings.
[Compatibly Achieving Both Machinability During Steel Piston Production and High Temperature Fatigue Strength and Toughness During Steel Piston Use]
The present inventors first conducted studies regarding the chemical composition of a steel material that is excellent in machinability when producing a steel piston, and is excellent in fatigue strength (high temperature fatigue strength) and toughness in a high-temperature region when using the steel piston. As a result, the present inventors discovered that if the chemical composition of a steel material consists of, in mass %, C: 0.15 to 0.30%, Si: 0.02 to 1.00%, Mn: 0.20 to 0.80%, P: 0.020% or less. S: 0.028% or less, Cr: 0.80 to 1.50%, Mo: 0.08 to 0.40%, V: 0.10 to 0.40%, Al: 0.005 to 0.060%, N: 0.0150% or less, O: 0.0030% or less, Cu: 0 to 0.50%, Ni: 0 to 1.00%. Nb: 0 to 0.100%, and the balance: Fe and impurities, and satisfies Formula (1) and Formula (2), the steel material is excellent in machinability when producing a steel piston, and can suppress a decrease in strength in a high-temperature region during use of the steel piston.
0.42≤Mo+3V≤1.50 (1)
V/Mo≥0.50 (2)
where, a content (mass %) of a corresponding element is substituted for each symbol of an element in Formula (1) and Formula (2). This point is described in detail hereunder.
A steel piston is produced, for example, by the following process. First, steel material for a steel piston is subjected to hot forging to produce intermediate products (an upper member, and a lower member). The intermediate products are subjected to a thermal refining treatment (quenching and tempering). After undergoing the thermal refining treatment, the upper member and the lower member are joined by friction joining or laser joining to produce a joined product. The joined product is subjected to machining such as cutting to produce a steel piston as an end product. Alternatively, the upper member and the lower member produced by hot forging are subjected to friction joining or laser joining to produce a joined product. A thermal refining treatment (quenching and tempering) is performed on the joined product. After undergoing the thermal refining treatment, the joined product is subjected to machining such as cutting to produce a steel piston as the end product. In short, production patterns for producing a steel piston include, for example, the following two patterns.
In the steel material for a steel piston of the present embodiment, in order to improve the machinability, an upper limit of the C content is kept to 0.30%. Subsequently, in the tempering during the thermal refining treatment process of the aforementioned production process, tempering is performed at a temperature (400 to 600° C.) of the same level as the surface temperature of the steel piston during engine operation. By this means, the hardness of the surface of the intermediate products after tempering can be lowered. Therefore, on the premise that a condition regarding the number of coarse Mn sulfides that is described later is satisfied, high machinability is obtained.
In addition, the steel material for a steel piston of the present embodiment contains Mo in an amount of 0.08 to 0.40% and V in an amount of 0.10 to 0.40% as aging precipitation elements during use of the steel piston. By containing these aging precipitation elements in combination, in a temperature region (500 to 600° C.) of the steel piston during use, fine carbides containing Mo and/or V are subjected to aging precipitation within the steel piston. By the aging precipitation that is caused by containing a combination of Mo and V, the high temperature strength of the steel piston during engine operation is secured. In this case, a decrease in the lifetime of the steel piston due to thermal fatigue can be suppressed.
To obtain this effect, the Mo content and the V content of the steel piston for a steel piston satisfy the following Formula (1) and Formula (2):
0.42≤Mo+3V≤1.50 (1)
V/Mo≥0.50 (2)
It is defined that F1=Mo+3V. F1 is an index that indicates the ability to strengthen the high temperature strength by aging precipitation of Mo and V. If F1 is less than 0.42, carbides containing Mo and/or V (Mo carbides, V carbides, and composite carbides containing Mo and V) cannot be subjected to aging precipitation sufficiently, and the desired high temperature strength of the steel material is not obtained. On the other hand, if F1 is more than 1.50, the effect is saturated, and the toughness of the steel material also decreases. If F1 satisfies Formula (1), on the premise that Formula (2) is satisfied, carbides containing Mo and/or V sufficiently precipitate, and the high temperature strength of the steel material increases. As a result, the fatigue strength at a high temperature also increases. In addition, the toughness of the steel material increases.
It is defined that F2=V/Mo. In a case where Mo and V in combination are contained so as to satisfy Formula (1), and F2 satisfies Formula (2), in comparison to a case where the steel material contains Mo and does not contain V or a case where the steel material contains V and does not contain Mo, a greater quantity of fine carbides containing Mo and/or V sufficiently precipitate in the temperature region of 400 to 600° C. As a result, the high temperature strength of the steel material increases further. Although the reason for this is uncertain, it is considered that the reason is as follows.
In a case where Mo alone is contained in the steel material, Mo forms carbides in a temperature region around 500° C. and is subjected to aging precipitation. In a case where V alone is contained in the steel material, V forms carbides in a temperature region around 600° C. that is higher than the temperature region for Mo, and is subjected to aging precipitation.
On the other hand, in a case where the steel material contains Mo and V in combination, Mo carbides precipitate in a temperature region around 500° C. In addition, when the Mo carbides precipitate, precipitation of V carbides that originally would precipitate at around 600° C. is induced by precipitation of the Mo carbides, and the V carbides precipitate as fine composite carbides containing Mo and V in a temperature region lower than 600° C. It is difficult for the composite carbides containing Mo and V to grow even if the temperature increases after precipitation, and the composite carbides are maintained as they are as fine composite carbides. In addition, in a temperature region around 600° C. V in a dissolved state that did not precipitate as composite carbides finely precipitates as carbides.
F2 is an index that indicates the ease with which composite carbides of Mo and V precipitate. If F2 is less than 0.50, composite carbides containing Mo and V do not sufficiently precipitate. Therefore, even if F1 satisfies Formula (1), sufficient high temperature strength will not be obtained. If F1 satisfies Formula (1) and F2 satisfies Formula (2), a decrease in strength in the high-temperature region of 400 to 600° ° C. can be suppressed, and excellent high temperature strength and high temperature fatigue strength are obtained.
Assuming a usage state as a steel piston, the steel material for a steel piston of the present embodiment having the aforementioned chemical composition and the steel material of the Comparative Example were subjected to quenching at 920° C., and thereafter were subjected to tempering at 600° ° C. (assumed usage temperature of a steel piston). Each steel material after tempering was subjected to a tensile test conforming to JIS Z2241 (2011) in a temperature range of 20° ° C. to 600° C. in the atmosphere, and yield strengths were obtained at respective temperatures.
Referring to
[Machinability and High Temperature Fatigue Strength of Steel Material Including HAZ Region by Control of Inclusions]
The present inventors further discovered that, in the steel material for a steel piston of the present embodiment, with respect to inclusions contained in the steel, if all of the following requirements (A) to (C) are satisfied, it is possible to secure (1) machinability during steel piston production, (2) high temperature fatigue strength during use of the steel piston, and (3) high temperature fatigue strength in a HAZ region during use of the steel piston.
(A) The number of Mn sulfides containing 10.0 mass % or more of Mn and containing 10.0 mass % or more of S is 100.0 per mm2 or less.
(B) Among the Mn sulfides, the number of coarse Mn sulfides that have an equivalent circular diameter of 3.0 μm or more is within the range of 1.0 to 10.0 per mm2.
(C) The number of oxides containing 10.0 mass % or more of oxygen is 15.0 per mm2 or less.
This point is described in detail hereunder.
In the steel material having the chemical composition of the present embodiment, Mn sulfides and oxides are present in the steel. In the present description. Mn sulfides and oxides are defined as follows.
Mn sulfides: inclusions containing 10.0 mass % or more of Mn and 10.0 mass % or more of S
Oxides: inclusions containing 10.0 mass % or more of O
Note that, in the present description, inclusions containing 10.0 mass % or more of Mn. 10.0 mass % or more of S, and 10.0 mass % or more of O (oxygen) are defined as “oxides”. In other words, in the present description, the term “Mn sulfides” means inclusions that contain 10.0 mass % or more of Mn and 10.0 mass % or more of S, and in which the O content is less than 10.0%.
In the present embodiment, as described in (A) and (C) above, the number of Mn sulfides and oxides that account for a major portion of the inclusions contained in the steel material is made as small as possible. As described above, in some cases a steel piston is formed by friction joining or laser joining. In such a case, a HAZ exists in the steel piston. In some cases, the fatigue strength in a high-temperature region (high temperature fatigue strength) of a HAZ is lower than the fatigue strength of other regions. To secure the high temperature fatigue strength of a HAZ, the number of Mn sulfides and oxides that are inclusions is lowered as much as possible.
On the other hand, the steel material for a steel piston also needs to have machinability. Mn sulfides enhance the machinability of the steel material. However, unless the Mn sulfides are of a certain size or more, the Mn sulfides will not contribute to machinability. Therefore, in the present embodiment, on the premise that (A) and (C) are satisfied, as described in (B) above, the number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more is made to fall within the range of 1.0 to 10.0 per mm2. In this case, while securing the number of coarse sulfides required for the machinability of the steel material for a steel piston by means of (B), the total number of inclusions contained in the steel is kept as low as possible by means of (A) and (C) and the high temperature fatigue strength of a HAZ of the steel piston is secured.
A steel material for a steel piston according to the present embodiment that has been completed based on the above findings has the following compositions.
[1] A steel material for a steel piston having a chemical composition which consists of, in mass %:
[2] The steel material for a steel piston according to [1], wherein:
Hereunder, the steel material for a steel piston according to the present embodiment is described in detail. The symbol “%” used in relation to elements means “mass %”, unless specifically stated otherwise.
[Chemical Composition]
The chemical composition of the steel material for a steel piston of the present embodiment contains the following elements.
C: 0.15 to 0.30%
Carbon (C) increases the strength of the steel material. If the C content is less than 0.15%, this effect will not be sufficiently obtained even when the contents of the other elements are within the ranges of the present embodiment. On the other hand, if the C content is more than 0.30%, even when the contents of the other elements are within the ranges of the present embodiment, the machinability of the steel material will decrease when producing the steel piston, and the toughness of the steel material will also decrease. Therefore, the C content is within the range of 0.15 to 0.30%. A preferable lower limit of the C content is 0.16%, more preferably is 0.17%, further preferably is 0.18%, and more preferably is 0.19%. A preferable upper limit of the C content is 0.29%, more preferably is 0.28%, further preferably is 0.27%, more preferably is 0.26%, and further preferably is 0.25%.
Si: 0.02 to 1.00%
Silicon (Si) deoxidizes the steel. In addition, Si increases the strength of ferrite. If the Si content is less than 0.02%, these effects will not be sufficiently obtained even when the contents of the other elements are within the ranges of the present embodiment. On the other hand, if the Si content is more than 1.00%, even when the contents of the other elements are within the ranges of the present embodiment, the machinability of the steel material will decrease when producing the steel piston. Therefore, the Si content is within the range of 0.02 to 1.00%. A preferable lower limit of the Si content is 0.03%, more preferably is 0.04%, further preferably is 0.10%, more preferably is 0.20%, and further preferably is 0.25%. A preferable upper limit of the Si content is 0.90%, more preferably is 0.85%, further preferably is 0.80%, and more preferably is 0.78%.
Mn: 0.20 to 0.80%
Manganese (Mn) enhances the hardenability of the steel material, and increases the strength of the steel material by solid-solution strengthening. If the Mn content is less than 0.20%, even when the contents of the other elements are within the ranges of the present embodiment, these effects will not be sufficiently obtained. On the other hand, if the Mn content is more than 0.80%, even when the contents of the other elements are within the ranges of the present embodiment, the machinability of the steel material will decrease. Therefore, the Mn content is within the range of 0.20 to 0.80%. A preferable lower limit of the Mn content is 0.21%, more preferably is 0.22%, further preferably is 0.25%, more preferably is 0.30%, and further preferably is 0.35%. A preferable upper limit of the Mn content is 0.79%, more preferably is 0.78%, further preferably is 0.77%, more preferably is 0.76%, and further preferably is 0.75%.
P: 0.020% or Less
Phosphorus (P) is an impurity that is unavoidably contained. In other words, the P content is more than 0%. If the P content is more than 0.020%, even when the contents of the other elements are within the ranges of the present embodiment. P will segregate at grain boundaries and will decrease the strength of the steel material. Therefore, the P content is 0.020% or less. A preferable upper limit of the P content is 0.019%, more preferably is 0.018%, further preferably is 0.017%, and more preferably is 0.015%. The P content is preferably as low as possible. However, excessively reducing the P content will incur a production cost. Therefore, when industrial production is taken into consideration, a preferable lower limit of the P content is 0.001%, and more preferably is 0.002%.
S: 0.028% or Less
Sulfur (S) is unavoidably contained. In other words, the S content is more than 0%. S combines with Mn to form Mn sulfides and enhances the machinability of the steel material. If even a small amount of S is contained, this effect is obtained to a certain extent. On the other hand, if the S content is more than 0.028%, even when the contents of the other elements are within the ranges of the present embodiment, coarse Mn sulfides will form or an excessive amount of Mn sulfides will form. In this case, the high temperature strength and high temperature fatigue strength will decrease. Therefore, the S content is 0.028% or less. A preferable lower limit of the S content for effectively obtaining the aforementioned effect is 0.001%, more preferably is 0.003%, further preferably is 0.005%, and more preferably is 0.009%. A preferable upper limit of the S content is 0.025%, more preferably is 0.023%, further preferably is 0.020%, more preferably is 0.019%, further preferably is 0.018%, and more preferably is 0.015%.
Cr: 0.80 to 1.50%
Chromium (Cr) enhances the strength of the steel material. If the Cr content is less than 0.80%, even when the contents of the other elements are within the ranges of the present embodiment, this effect will not be sufficiently obtained. On the other hand, if the Cr content is more than 1.50%, even when the contents of the other elements are within the ranges of the present embodiment, Cr carbides will form and the fatigue strength at a high temperature will decrease. In addition, if the Cr content is more than 1.50%, the machinability of the steel material will decrease. Therefore, the Cr content is within the range of 0.80 to 1.50%. A preferable lower limit of the Cr content is 0.82%, more preferably is 0.84%, further preferably is 0.90%, and more preferably is 0.95%. A preferable upper limit of the Cr content is 1.45%, more preferably is 1.42%, further preferably is 1.40%, more preferably is 1.38%, and further preferably is 1.36%.
Mo: 0.08 to 0.40%
Molybdenum (Mo) is subjected to aging precipitation together with V, described later, in a usage temperature range (500 to 600° C.) of the steel piston, and forms precipitates. By this means, the high temperature strength and high temperature fatigue strength of the steel piston in an engine operating state can be maintained at a high level. If the Mo content is less than 0.08%, even when the contents of the other elements are within the ranges of the present embodiment, this effect will not be sufficiently obtained. On the other hand, if the Mo content is more than 0.40%, even when the contents of the other elements are within the ranges of the present embodiment, the strength of the steel material will become excessively high, and the toughness will decrease. Therefore, the Mo content is within the range of 0.08 to 0.40%. A preferable lower limit of the Mo content is 0.09%, more preferably is 0.10%, further preferably is 0.11%, more preferably is 0.12%, and further preferably is 0.13%. A preferable upper limit of the Mo content is 0.39%, more preferably is 0.38%, further preferably is 0.36%, more preferably is 0.34% and further preferably is 0.32%.
V: 0.10 to 0.40%
Vanadium (V) is subjected to aging precipitation together with the aforementioned Mo in a usage temperature range (500 to 600° C.) of the steel piston, and forms precipitates. By this means, the high temperature strength and fatigue strength of the steel piston in an engine operating state can be maintained at a high level. If the V content is less than 0.10%, even when the contents of the other elements are within the ranges of the present embodiment, this effect will not be sufficiently obtained. On the other hand, if the V content is more than 0.40%, even when the contents of the other elements are within the ranges of the present embodiment, the strength of the steel material will become excessively high, and the toughness will decrease. Therefore, the V content is within the range of 0.10 to 0.40%. A preferable lower limit of the V content is 0.11%, more preferably is 0.12%, further preferably is 0.13%, and more preferably is 0.14%. A preferable upper limit of the V content is 0.39%, more preferably is 0.38%, further preferably is 0.37%, more preferably is 0.36% and further preferably is 0.35%.
Al: 0.005 to 0.060%
Aluminum (Al) deoxidizes the steel. If the Al content is less than 0.005%, even when the contents of the other elements are within the ranges of the present embodiment, this effect will not be obtained. On the other hand, if the Al content is more than 0.060%, even when the contents of the other elements are within the ranges of the present embodiment, oxides (inclusions) will excessively form, and the high temperature strength and high temperature fatigue strength of a steel piston that includes a HAZ will decrease. Therefore, the Al content is within the range of 0.005 to 0.060%. A preferable lower limit of the Al content is 0.007%, more preferably is 0.008%, further preferably is 0.010%, more preferably is 0.012%, and further preferably is 0.014%. A preferable upper limit of the Al content is 0.058%, more preferably is 0.056%, further preferably is 0.052%, more preferably is 0.050%, further preferably is 0.048% and more preferably is 0.045%.
N: 0.0150% or Less
Nitrogen (N) is an impurity that is unavoidably contained. In other words, the N content is more than 0%. If the N content is more than 0.0150%, even when the contents of the other elements are within the ranges of the present embodiment, the hot workability of the steel material will decrease. Therefore, the N content is 0.0150% or less. A preferable upper limit of the N content is 0.0140%, more preferably is 0.0130%, further preferably is 0.0125%, and more preferably is 0.0120%. The N content is preferably as low as possible. However, excessively reducing the N content will incur a production cost. Therefore, when industrial production is taken into consideration, a preferable lower limit of the N content is 0.0010%, and more preferably is 0.0015%.
O: 0.0030% or Less
Oxygen (O) is an impurity that is unavoidably contained. In other words, the O content is more than 0%. If the O content is more than 0.0030%, even when the contents of the other elements are within the ranges of the present embodiment, oxides will excessively form, and the high temperature strength and fatigue strength of a steel piston that includes a HAZ region will decrease. Therefore, the O content is 0.0030% or less. A preferable upper limit of the O) content is 0.0028%, more preferably is 0.0026%, further preferably is 0.0022%, more preferably is 0.0020%, and further preferably is 0.0018%. The O content is preferably as low as possible. However, excessively reducing the O content will incur a production cost. Therefore, when industrial production is taken into consideration, a preferable lower limit of the O content is 0.0005%, and more preferably is 0.0010%.
Balance: Fe and Impurities
The balance of the chemical composition of the steel material for a steel piston according to the present embodiment is Fe and impurities. Here, the term “impurities” refers to components which, during industrial production of the steel material for a steel piston, are mixed in from ore or scrap used as a raw material or from the production environment or the like, and which are not components that are intentionally contained in the steel.
All elements other than the aforementioned impurities may be mentioned as examples of impurities. The balance may include only one kind of impurity or may include two or more kinds of impurity. Examples of impurities other than the aforementioned impurities include Ca, B, Sb, Sn, W, Co, As, Pb, Bi and H. It is possible for a case to arise in which these elements are contained, for example, as impurities having the following contents.
Ca: 0 to 0.0005%, B: 0 to 0.0005%, Sb: 0 to 0.0005%, Sn: 0 to 0.0005%, W: 0 to 0.0005%, Co: 0 to 0.0005%, As: 0 to 0.0005%, Pb: 0 to 0.0005%, Bi: 0 to 0.0005% and H: 0 to 0.0005%.
[Regarding Optional Elements]
The aforementioned steel material for a steel piston may also contain one or more elements selected from the group consisting of Cu: 0 to 0.50%, Ni: 0 to 1.00% and Nb: 0 to 0.100% in lieu of a part of Fe.
Cu: 0 to 0.50%
Copper (Cu) is an optional element, and need not be contained. In other words, the Cu content may be 0%. When contained, Cu enhances the hardenability of the steel material and increases the strength of the steel material. As long as the Cu content is more than 0%, these effects will be obtained to a certain extent. On the other hand, if the Cu content is more than 0.50%, even when the contents of the other elements are within the ranges of the present embodiment, the hot workability of the steel material will decrease. Therefore, the Cu content is within the range of 0 to 0.50%. A preferable lower limit of the Cu content for more effectively enhancing the aforementioned effects is 0.01%, more preferably is 0.02%, further preferably is 0.04%, and more preferably is 0.05%. A preferable upper limit of the Cu content is 0.48%, more preferably is 0.46%, further preferably is 0.44%, and more preferably is 0.40%.
Ni: 0 to 1.00%
Nickel (Ni) is an optional element, and need not be contained. In other words, the Ni content may be 0%. When contained, Ni enhances the hardenability of the steel material and increases the strength of the steel material. As long as the Ni content is more than 0%, these effects will be obtained to a certain extent. On the other hand, if the Ni content is more than 1.00%, even when the contents of the other elements are within the ranges of the present embodiment, the effect of the Ni will be saturated and, in addition, the cost of the raw materials will increase. Therefore, the Ni content is within the range of 0 to 1.00%. A preferable lower limit of the Ni content for effectively obtaining the aforementioned effects is 0.01%, more preferably is 0.02%, further preferably is 0.04%, and more preferably is 0.05%. A preferable upper limit of the Ni content is 0.98%, more preferably is 0.90%, further preferably is 0.85%, more preferably is 0.80%, further preferably is 0.70%, and more preferably is 0.60%.
Nb: 0 to 0.100%
Niobium (Nb) is an optional element, and need not be contained. In other words, the Nb content may be 0%. When contained. Nb forms carbides, nitrides or carbo-nitrides (hereinafter, referred to as “carbo-nitrides or the like”) in the steel material, and increases the strength of the steel material. As long as the Nb content is more than 0%, these effects will be obtained to a certain extent. On the other hand, if the Nb content is more than 0.100%, even when the contents of the other elements are within the ranges of the present embodiment, the strength of the steel material will become too high, and the machinability of the steel material during steel piston production will decrease. Therefore, the Nb content is within the range of 0 to 0.100%. A preferable lower limit of the Nb content for effectively obtaining the aforementioned effects is 0.010%, more preferably is 0.015%, and further preferably is 0.020%. A preferable upper limit of the Nb content is 0.095%, more preferably is 0.090%, further preferably is 0.085%, more preferably is 0.080%, and further preferably is 0.070%.
[Regarding Formula (1) and Formula (2)]
The chemical composition of the steel material for a steel piston of the present embodiment also satisfies Formula (1) and Formula (2).
0.42≤Mo+3V≤1.50 (1)
V/Mo≥0.50 (2)
It is defined that F1=Mo+3V. F1 is an index that indicates the ability to strengthen the high temperature strength by aging precipitation of Mo and V.
If F1 is less than 0.42, carbides containing Mo and/or V (Mo carbides. V carbides, and composite carbides containing Mo and V) cannot be subjected to aging precipitation sufficiently. Therefore, the desired high temperature strength of the steel material is not obtained. On the other hand, if F1 is more than 1.50, the effect is saturated and the toughness of the steel material also decreases. If F1 is within the range of 0.42 to 1.50, that is, if F1 satisfies Formula (1), on the premise that Formula (2) is satisfied, carbides containing Mo and/or V will sufficiently precipitate, and the high temperature strength and high temperature fatigue strength of the steel material will increase, and the toughness thereof will also increase. A preferable lower limit of F1 is 0.45, more preferably is 0.47, further preferably is 0.50, more preferably is 0.55, further preferably is 0.60, and more preferably is 0.62. A preferable upper limit of F1 is 1.48, more preferably is 1.46, further preferably is 1.42, more preferably is 1.40, further preferably is 1.36, more preferably is 1.34, and further preferably is 1.30.
[Regarding Formula (2)]
As described above, in the steel material for a steel piston of the present embodiment, fine composite carbides containing Mo and V are subjected to aging precipitation in a large quantity in a temperature region from 500 to 600° C. By this means, in comparison to a case where the steel material contains Mo and does not contain V, or a case where the steel material contains V and does not contain Mo, in the steel material for a steel piston of the present embodiment, a greater quantity of fine aging precipitates can be caused to precipitate. As a result, the high temperature strength and the high temperature fatigue strength of the steel material are enhanced.
It is defined that F2=V/Mo. F2 is an index that indicates the ease with which composite carbides of Mo and V precipitate. If F2 is less than 0.50, composite carbides containing Mo and V do not sufficiently precipitate. Therefore, even if F1 satisfies Formula (1), sufficient high temperature strength will not be obtained. If F1 satisfies Formula (1) and F2 satisfies Formula (2), a decrease in strength in the high-temperature region of 500 to 600° C. can be suppressed, and excellent high temperature strength and high temperature fatigue strength are obtained. A preferable lower limit of F2 is 0.52, more preferably is 0.55, further preferably is 0.57, more preferably is 0.60, further preferably is 0.65, and more preferably is 0.70.
[Regarding Inclusions (Mn Sulfides and Oxides) Contained in Steel Material for Steel Piston]
In the steel material for a steel piston according to the present embodiment, at a cross section parallel to the axial direction (longitudinal direction) of the steel material for a steel piston, Mn sulfides and oxides in the steel material also satisfy the following conditions.
(A) The number of Mn sulfides containing 10.0 mass % or more of Mn and containing 10.0 mass % or more of S is 100.0 per mm2 or less.
(B) Among the Mn sulfides, the number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more is within the range of 1.0 to 10.0 per mm2.
(C) The number of oxides containing 10.0 mass % or more of oxygen is 15.0 per mm2 or less.
In the present description, Mn sulfides and oxides are defined as follows.
Mn sulfides: inclusions containing 10.0 mass % or more of S and 10.0 mass % or more of Mn
Oxides: inclusions containing 10.0 mass % or more of O (oxygen)
Note that, in the present description, inclusions containing 10.0 mass % or more of Mn, 10.0 mass % or more of S, and 10.0 mass % or more of O) are defined as “oxides”. In other words, in the present description, the term “Mn sulfides” means inclusions that contain 10.0 mass % or more of Mn and 10.0 mass % or more of S, and in which the O content is less than 10.0%.
[Regarding Number of Mn Sulfides and Oxides (Aforementioned (A) and (C))]
In the present embodiment, as described in (A) above, the number of Mn sulfides is 100.0 per mm2 or less. In addition, as described in (C) above, the number of oxides is 15.0 per mm2 or less.
In the steel material for a steel piston of the present embodiment, as described in the aforementioned (A) and (C), the number of Mn sulfides and oxides that account for a major portion of the inclusions contained in the steel material is made as small as possible. As described above, in some cases the steel piston is formed by friction joining or laser joining. In such a case, a HAZ will exist inside the steel piston. In some cases, the high temperature fatigue strength of a HAZ is lower than the fatigue strength of other regions. To secure the high temperature fatigue strength of a HAZ, the number of Mn sulfides and oxides that are inclusions is reduced as much as possible.
[Regarding Number of Coarse Sulfides (Aforementioned (B))]
In the present embodiment, in addition, as described in the above (B), among the Mn sulfides, the number of coarse Mn sulfides that have an equivalent circular diameter of 3.0 μm or more is within the range of 1.0 to 10.0 per mm2.
As described above, inclusions are reduced as much as possible in order to secure the high temperature fatigue strength of a HAZ in a case where the steel piston is formed by performing friction joining or laser joining. However, it is also necessary for the steel material for a steel piston to have machinability. Although Mn sulfides enhance the machinability of the steel material, unless the Mn sulfides are of a certain size or more, the Mn sulfides will not contribute to machinability. Therefore, in the present embodiment, on the premise that (A) and (C) are satisfied, as described in (B) above, the number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more is made to fall within the range of 1.0 to 10.0 per mm2. The term “coarse sulfides” specified in (B) means sulfides having an equivalent circular diameter of 3.0 μm or more. The term “equivalent circular diameter” means the diameter of a circle in a case where the area of a sulfide at a cross section parallel to the axial direction (longitudinal direction) of the steel material for a steel piston is converted into a circle having the same area. In this case, while securing the number of coarse sulfides required for the machinability of the steel material for the steel piston by means of (B), the total number of inclusions contained in the steel is kept as low as possible by means of (A) and (C) to thereby secure the high temperature fatigue strength of a HAZ of the steel piston.
A preferable number of Mn sulfides is 90.0 per mm2 or less, more preferably is 85.0 per mm2 or less, further preferably is 82.0 per mm2 or less, more preferably is 80.0 per mm2 or less, and further preferably is 78.0 per mm2 or less.
A preferable lower limit of the number of coarse Mn sulfides (Mn sulfides having an equivalent circular diameter of 3.0 μm or more) is 1.5 per mm2, more preferably is 2.0 per mm2, further preferably is 2.5 per mm2, and more preferably is 3.0 per mm2. A preferable upper limit of the number of coarse Mn sulfides is 9.0 per mm2, more preferably is 8.5 per mm2, further preferably is 8.0 per mm2, and more preferably is 7.5 per mm2.
A preferable number of oxides is 13.0 per mm2 or less, more preferably is 10.0 per mm2 or less, further preferably is 9.0 per mm2 or less, and more preferably is 8.0 per mm2 or less.
[Method for Measuring Mn Sulfides and Oxides]
The number of Mn sulfides (number per mm2), the number of coarse Mn sulfides (number per mm2) having an equivalent circular diameter of 3.0 μm or more, and the number of oxides (number per mm2) in the steel can be measured by the following method.
A sample is taken from the steel material for a steel piston. In a case where the steel material for a steel piston is a steel bar, as illustrated in
Using a scanning electron microscope (SEM), 20 visual fields (evaluation area per visual field is 100 μm×100 μm) on the observation surface of the sample taken are observed randomly at a magnification of ×1000.
In the respective visual fields, inclusions are identified. Each of the identified inclusions is subjected to point analysis using energy dispersive X-ray spectroscopy (EDX) to identify Mn sulfides and oxides. Specifically, in the elementary analysis results for the identified inclusions, in a case where the Mn content is 10.0 mass % or more and the S content is 10.0 mass % or more, the relevant inclusion is defined as an Mn sulfide. Further, in the elementary analysis results for the identified inclusions, in a case where the O content is 10.0 mass % or more, the relevant inclusion is defined as an oxide. Note that, an inclusion containing 10.0 mass % or more of Mn, 10.0 mass % or more of S, and 10.0 mass % or more of O is defined as an oxide.
Inclusions that are taken as the target of the aforementioned identification are inclusions having an equivalent circular diameter of 0.5 μm or more. Here, the term “equivalent circular diameter” means the diameter of a circle in a case where the area of each inclusion is converted into a circle having the same area.
If the inclusions have an equivalent circular diameter that is two times or more larger than the beam diameter of EDX, the accuracy of the elementary analysis will be increased. In the present embodiment, the beam diameter of the EDX used to identify inclusions is set to 0.2 μm. In this case, the accuracy of elementary analysis using EDX cannot be increased by inclusions that have an equivalent circular diameter that is less than 0.5 μm. In addition, inclusions that have an equivalent circular diameter of less than 0.5 μm have extremely small influence on strength. Therefore, in the present embodiment, Mn sulfides and oxides having an equivalent circular diameter of 0.5 μm or more are taken as the identification target. Note that, the upper limit of the equivalent circular diameter of the inclusions is not particularly limited, and for example is 100 μm.
The number of Mn sulfides per unit area (number per mm2) is determined based on the total number of Mn sulfides identified in the 20 visual fields and the total area of the 20 visual fields. Further, among the Mn sulfides identified in the 20 visual fields, the total number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more is determined. The number of coarse Mn sulfides per unit area (number per mm2) is then determined based on the total number of coarse Mn sulfides and the total area of the 20 visual fields. Furthermore, the number of oxides per unit area (number per mm2) is determined based on the total number of oxides identified in the 20 visual fields and the total area of the 20 visual fields.
[Production Method]
An example of a method for producing the steel material for a steel piston according to the present embodiment will now be described. In the present embodiment, a method for producing a steel bar as one example of a steel material for a steel piston is described. However, the steel material for the steel piston of the present embodiment is not limited to a steel bar. The steel material for a steel piston of the present embodiment may also be, for example, a pipe.
One example of a production method includes a steel making process of refining and casting molten steel to produce a starting material (a cast piece or an ingot), and a hot working process of subjecting the starting material to hot working to produce the steel material for a steel piston. Hereunder, each of these processes is described.
[Steel Making Process]
The steel making process includes a refining process and a casting process.
[Refining Process]
In the refining process, firstly, hot metal produced by a well-known method is subjected to refining (primary refining) using a converter. Molten steel tapped from the converter is subjected to secondary refining. In the secondary refining, alloying elements for composition adjustment are added to thereby produce a molten steel satisfying the aforementioned chemical composition.
Specifically, Al is added to the molten steel tapped from the converter to perform a deoxidation treatment. After the deoxidation treatment, a deslagging treatment is performed. After the deslagging treatment, secondary refining is performed. In the secondary refining, composite refining is performed. First, secondary refining that uses an LF (ladle furnace) is performed. In addition, an RH (Ruhrstahl-Hausen) vacuum degassing treatment is performed. Thereafter, final composition adjustment of the molten steel is performed.
In this case, the basicity of the slag (=CaO in slag/SiO2 in slag (mass ratio)) in the LF is adjusted to within the following range.
Slag basicity: 2.5 to 4.5
In the present embodiment, in order to satisfy the requirements for inclusions described in (A) to (C) above, the basicity of the slag in the LF is adjusted to within the range of 2.5 to 4.5. In a case where the slag basicity is within the range of 2.5 to 4.5, Ca contained in the slag dissolves in the molten steel, and Mn sulfides and oxides are formed. By means of this slight amount of Ca that dissolved in the molten steel, coarsening of Mn sulfides and oxides is suppressed and the number of these inclusions (Mn sulfides and oxides) is also kept to a low number. In addition, the number of coarse Mn sulfides satisfies the aforementioned (B).
If the slag basicity in the LF is less than 2.5, the number of Mn sulfides will be more than 100.0 per mm2 or the number of oxides will be more than 15.0 per mm2 or the number of coarse Mn sulfides will be more than 10.0 per mm2.
On the other hand, if the slag basicity in the LF is more than 4.5, because formation of coarse Mn sulfides will be suppressed, the number of coarse Mn sulfides will be less than 1.0 per mm2.
A preferable lower limit of the slag basicity in the LF is 2.6, and more preferably is 2.7. A preferable upper limit of the slag basicity in the LF is 4.4, and more preferably is 4.3.
Note that, the molten steel temperature in the LF is, for example, 1500 to 1600° C. After performing the aforementioned secondary refining, adjustment of the components of the molten steel is performed by a well-known method.
[Casting Process]
In the casting process, a starting material (a cast piece or an ingot) is produced using the molten steel produced by the above refining process. Specifically, a cast piece is produced by a continuous casting process using the molten steel. Alternatively, an ingot may be produced by an ingot-making process using the molten steel.
[Hot Working Process]
In the hot working process, the produced starting material is subjected to hot working to produce a steel material for a steel piston. In the hot working process, hot working is usually performed once or a plurality of times. In the case of performing hot working a plurality of times, the initial hot working (rough working process) is, for example, blooming or hot forging. The next hot working (finishing process) is, for example, finish rolling using a continuous mill. In the continuous mill, a horizontal stand having a pair of horizontal rolls, and a vertical stand having a pair of vertical rolls are alternately arranged in a row.
In a case where the hot working process includes a rough working process and a finishing process, the heating temperature of the starting material during the rough working process is set to within the range of 1000 to 1300° C. Further, when using a continuous mill in the finishing process, the temperature of the starting material on the exit side of the final stand that rolls the starting material is defined as the rolling finishing temperature. In this case, the rolling finishing temperature is set within the range of 850 to 1100° C. The steel material after the finishing process is cooled until becoming room temperature. The cooling method is not particularly limited. The cooling method is, for example, allowing the steel material to cool in the air.
Note that, the microstructure of the steel material for a steel piston of the present embodiment is not particularly limited. In a method for producing a steel piston that is described later, the steel material for a steel piston of the present embodiment is heated to the Ac3 transformation point or higher prior to hot forging. Therefore, the microstructure of the steel material for a steel piston of the present embodiment is not particularly limited. For example, at an R/2 position in a cross section perpendicular to the axial direction (longitudinal direction) of the steel material for a steel piston, the total area fraction of ferrite and pearlite is 80% or more, and the balance is bainite or martensite. However, the microstructure of the steel material for a steel piston of the present embodiment is not particularly limited to the aforementioned microstructure.
A steel material for a steel piston according to the present embodiment can be produced by the above processes.
[Method for Producing Steel Piston]
An example of a method for producing a steel piston using the steel material for a steel piston of the present embodiment that is described above will now be described.
For example, the following two patterns are available with respect to a method for producing the steel piston of the present embodiment.
According to pattern 1, the steel piston is produced as follows. First, the steel material for a steel piston is subjected to hot forging to produce an upper member and a lower member that are intermediate products (hot forging process). The heating temperature of the steel material for a steel piston during hot forging is 1100 to 1250° C. Here, the term “heating temperature” means the furnace temperature of the heating furnace.
The thus-produced upper member and lower member are subjected to a well-known thermal refining treatment (quenching and tempering) (thermal refining treatment process). The quenching is performed at a well-known quenching temperature (A3 transformation point or higher), followed by rapidly cooling. The rapidly cooling is, for example, water cooling or oil cooling. The tempering is also performed at a well-known tempering temperature (AC1 transformation point or lower). After undergoing the thermal refining treatment process, the upper member and the lower member are subjected to well-known friction joining or laser joining to produce a joined product in which the upper member and the lower member are joined (joining process). The joined product is subjected to machining such as cutting (machining process) to produce a steel piston as the end product.
According to pattern 2, a steel piston is produced as follows. The steel material for a steel piston is subjected to hot forging to produce an upper member and a lower member that are intermediate products (hot forging process). The conditions of the hot forging process are the same as in pattern 1. The upper member and the lower member are subjected to well-known friction joining or laser joining to produce a joined product in which the upper member and the lower member are joined (joining process). The joined product is subjected to a well-known thermal refining treatment (quenching and tempering) (thermal refining treatment process). The conditions of the quenching and tempering are the same as in pattern 1. After undergoing the thermal refining treatment, the joined product is subjected to machining such as cutting (machining process) to produce a steel piston as the end product.
Molten steels having the chemical compositions shown in Table 1 were produced.
The symbol “−” in Table 1 means that the corresponding element content was less than the detection limit. Further, F1 values are listed in an “F1” column, and F2 values are listed in an “F2” column. The molten steels having the chemical compositions of the respective test numbers were subjected to primary refining using a converter by a well-known method. In addition, after the molten steel was tapped from the converter, Al was added to the molten steel to perform a well-known deoxidation treatment. Further, after the deoxidation treatment, a well-known deslagging treatment was performed. After the deslagging treatment, secondary refining was performed. First, secondary refining using an LF was performed. Thereafter, a well-known RH vacuum degassing treatment was performed. After the RH treatment, final composition adjustment of the molten steel is performed. Note that, for the molten steel of each test number, the basicity of the slag in the LF was as shown in Table 2. The molten steel temperature in the LF was within the range of 1500 to 1600° C.
Cast pieces were produced by a continuous casting process using the respective molten steels after the secondary refining. Each produced cast piece was subjected to blooming to produce a billet. The heating temperature before blooming of the cast piece of each test number was within the range of 1000 to 1200° C. In addition, after blooming, each billet was subjected to finish rolling using a continuous mill. The rolling finishing temperature of each test number was within the range of 850 to 1100° C. After undergoing the finish rolling, the steel material was allowed to cool in air. Ay the above processes, a steel material for a steel piston was produced that was a steel bar with a diameter of 40 mm.
[Evaluation Tests]
The following evaluation tests were conducted using the thus-produced steel material for a steel piston (steel bar) of each test number.
[Mn Sulfides and Oxides Measurement Test]
The number of Mn sulfides (number per mm2), the number of coarse Mn sulfides (number per mm2) having an equivalent circular diameter of 3.0 μm or more, and the number of oxides (number per mm2) in the steel bar of each test number were measured by the following method.
A sample was taken from the steel material for a steel piston (steel bar) of each test number. As illustrated in
Using an SEM, 20 visual fields (evaluation area per visual field was 100 μm×100 μm) on the observation surface of each sample taken were observed randomly at a magnification of ×1000. Inclusions were identified in the respective visual fields. Each of the identified inclusions was subjected to point analysis using energy dispersive X-ray spectroscopy (EDX), and Mn sulfides and oxides were identified. Specifically, in the elementary analysis results for the identified inclusions, in a case where the Mn content was 10.0 mass % or more and the S content was 10.0 mass % or more, the relevant inclusion was defined as an Mn sulfide. Further, in the elementary analysis results for the identified inclusions, in a case where the O content was 10.0 mass % or more, the relevant inclusion was defined as an oxide. Note that, an inclusion containing 10.0 mass % or more of Mn, 10.0 mass % or more of S. and 10.0 mass % or more of O was defined as an oxide.
The inclusions taken as the target of the identification were inclusions having an equivalent circular diameter of 0.5 μm or more. Further, the beam diameter of the EDX used to identify the inclusions was set to 0.2 μm. The number of Mn sulfides per unit area (number per mm2) was determined based on the total number of Mn sulfides identified in the 20 visual fields and the total area of the 20 visual fields. The total number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more among the Mn sulfides identified in the 20 visual fields was determined. Further, the number of coarse Mn sulfides per unit area (number per mm2) was determined based on the total number of coarse Mn sulfides and the total area of the 20 visual fields. Furthermore, the number of oxides per unit area (number per mm2) was determined based on the total number of oxides identified in the 20 visual fields and the total area of the 20 visual fields. The number of Mn sulfides per unit area (number per mm2), the number of coarse Mn sulfides per unit area (number per mm2), and the number of oxides per unit area (number per mm2) obtained are shown in Table 2.
[Machinability Test]
A cutting test was conducted on the steel material for a steel piston of each test number by the following method, and the machinability of the steel material was evaluated.
First, a process for producing a simulated steel piston was performed with respect to the steel material of each test number to thereby prepare cutting test specimens. Specifically, a steel material for a steel piston (steel bar) with a diameter of 40 mm of each test number was heated for 30 minutes at a heating temperature of 1200° C. After being heated, the steel bar was subjected to hot forging to produce a round bar with a diameter of 30 mm. The finishing temperature in the hot forging was 950° ° C. or more for each test number.
The produced round bar was subjected to a thermal refining treatment. Specifically, the round bar was heated for one hour at a heating temperature of 950° C., and thereafter was immersed in an oil bath at an oil temperature of 80° ° C. and quenched. After quenching, the round bar was subjected to tempering. In the tempering, the round bar after quenching was held for one hour at a heating temperature of 600° C., and thereafter was allowed to cool in the atmosphere.
After undergoing the aforementioned thermal refining treatment (quenching and tempering), the round bar was subjected to machining to prepare a cutting test specimen having a diameter of 20 mm and a length of 40 mm. The central axis of the cutting test specimen approximately matched the central axis of the round bar after the thermal refining treatment.
A cutting test was conducted under the following conditions using the prepared cutting test specimens. With respect to the chip, an uncoated chip in which the base metal material was P20 grade carbide was used. The cutting conditions were as follows.
The average width of flank wear VB (μm) was measured as the amount of wear of the main cutting blade of the flank of the chip after a cutting time of 10 minutes passed. The average width of flank wear VB of the chip in Test Number 24 was adopted as a reference value. If the average width of flank wear VB of the chip of the respective test numbers was 100% or less relative to the reference value, it was determined that excellent machinability was obtained. Note that, the material quality of the steel material of Test Number 24 was equivalent to 42CrMo4 of the ISO standard, and the Vickers hardness Hv (test force: 9.8 N) in accordance with JIS Z 2244 (2009) was 300.
[High Temperature Fatigue Strength Test]
A high-temperature Ono type rotating bending fatigue test was conducted on the steel material for a steel piston of each test number, and the fatigue strength was evaluated. Specifically, first a process for producing a simulated steel piston was performed with respect to the steel material of each test number to thereby prepare high-temperature Ono type rotating bending fatigue test specimens.
Specifically, a steel bar with a diameter of 40 mm of each test number was heated for 30 minutes at a heating temperature of 1200° C. After being heated, the steel bar was subjected to hot forging to produce a round bar with a diameter of 30 mm. The finishing temperature in the hot forging was 950° ° C. or more for each test number.
After the hot forging, the round bar was subjected to a thermal refining treatment. Specifically, the round bar was heated for one hour at a heating temperature of 950° C., and thereafter was immersed in an oil bath at an oil temperature of 80° C. and quenched. After quenching, the round bar was subjected to tempering. In the tempering, the round bar after quenching was held for one hour at a heating temperature of 600° C. and thereafter was allowed to cool in the atmosphere.
A high-temperature Ono type rotating bending fatigue test specimen was prepared from a central part of a cross section perpendicular to the axial direction (longitudinal direction) of the round bar after thermal refining treatment. The central axis of the high-temperature Ono type rotating bending fatigue test specimen approximately matched the central axis of the round bar after the thermal refining treatment. The diameter of a parallel portion of the high-temperature Ono type rotating bending fatigue test specimen was 8 mm, and the length of the parallel portion was 15.0 mm.
A high-temperature Ono type rotating bending fatigue test was conducted under the following conditions using the thus-prepared high-temperature Ono type rotating bending fatigue test specimens. The evaluation temperature was set to 500° C. The test specimen was mounted in a testing machine inside a heating furnace, and thereafter increasing of the temperature of the heating furnace was started while rotating at 2500 rpm. After the indicated value of the furnace thermometer of the heating furnace reached 500° C. the test specimen was held for 30 minutes at 500° C. After being held for 30 minutes, a load was applied to start the fatigue test. The stress ratio was set to −1, and the maximum number of repetitions was set to 1×107 times. The endurance stress at the maximum number of repetitions (1×107 times) was defined as the fatigue strength (MPa). The obtained fatigue strength (MPa) for each test number is shown in Table 2. If the fatigue strength was 420 MPa or more, it was determined that excellent high temperature fatigue strength was obtained.
[Joint High Temperature Fatigue Strength Test]
For each test number, the high temperature fatigue strength of a joint of the round bar joined by friction joining was evaluated by the following method.
First, a process for producing a simulated steel piston was performed with respect to the steel material of each test number to thereby prepare joined round bar specimens. Specifically, a steel bar with a diameter of 40 mm of each test number was heated for 30 minutes at a heating temperature of 1200° C. After being heated, the steel bar was subjected to hot forging to produce a round bar with a diameter of 30 mm. The finishing temperature in the hot forging was 950° C. or more for each test number.
After the hot forging, the round bar was subjected to a thermal refining treatment. Specifically, the round bar was heated for one hour at a heating temperature of 950° ° C., and thereafter was immersed in an oil bath at an oil temperature of 80° ° C. and quenched. After quenching, the round bar was subjected to tempering. In the tempering, the round bar after quenching was held for one hour at a heating temperature of 600° C., and thereafter was allowed to cool in the atmosphere.
Machining was performed with respect to the axial direction (longitudinal direction) of each round bar after the thermal refining treatment to prepare two rough round bar specimens having a diameter of 20 mm and a length of 150 mm for each test number. The central axis of each of the two rough specimens prepared approximately matched the central axis of the round bar after the thermal refining treatment. The ends of the two rough round bar specimens were butted together, and friction joining was performed to prepare a joined round bar specimen. In the friction joining, the friction pressure was set to 100 MPa and the friction time was set to 5 seconds. The upset pressure (applied pressure from the two ends of the round bars to the joint) was set to 200 MPa, and the upset time was set to 5 seconds. The rotation speed during friction joining was set to 2000 rpm, and the burn-off length was set within the range of 5 to 12 mm. A joined round bar specimen was prepared by the above processes.
Machining (lathe turning) was performed to prepare a high-temperature Ono type rotating bending fatigue test specimen from a central part of a cross section perpendicular to the longitudinal direction of the joined round bar specimen. The central axis of the high-temperature Ono type rotating bending fatigue test specimen matched the central axis of the joined round bar specimen. The diameter of a parallel portion of the high-temperature Ono type rotating bending fatigue test specimen was 8 mm, and the length of the parallel portion was 15.0 mm. The center position in the axial direction of the parallel portion of the high-temperature Ono type rotating bending fatigue test specimen corresponded to the joining position.
A high-temperature Ono type rotating bending fatigue test was conducted under the following conditions using the thus-prepared high-temperature Ono type rotating bending fatigue test specimens. The evaluation temperature was set to 500° C. The test specimen was mounted in a testing machine inside a heating furnace, and thereafter increasing of the temperature of the heating furnace was started while rotating at 2500 rpm. After the indicated value of the furnace thermometer of the heating furnace reached 500° C., the test specimen was held for 30 minutes at 500° C. After being held for 30 minutes, a load was applied to start the fatigue test. The stress ratio was set to −1, and the maximum number of repetitions was set to 1×107 times. The endurance stress at the maximum number of repetitions (1×107 times) was defined as the fatigue strength (MPa). The obtained fatigue strength (MPa) for each test number is shown in Table 2. If the fatigue strength was 360 MPa or more, it was determined that excellent high temperature fatigue strength was obtained.
[Toughness Evaluation Test]
For each test number, the toughness of the steel material after thermal refining treatment was evaluated by the following method. First, a process for producing a simulated steel piston was performed with respect to the steel material of each test number to thereby prepare Charpy test specimens. Specifically, a steel bar with a diameter of 40 mm of each test number was heated for 30 minutes at a heating temperature of 1200° C. After being heated, the steel bar was subjected to hot forging to produce a round bar with a diameter of 20 mm. The finishing temperature in the hot forging was 950° ° C. or more for each test number.
After the hot forging, the round bar was subjected to a thermal refining treatment. Specifically, the round bar was heated for one hour at a heating temperature of 950° C. After being heated, the round bar was immersed in an oil bath at an oil temperature of 80° C. and quenched. After quenching, the round bar was subjected to tempering. In the tempering, the round bar after quenching was held for one hour at a heating temperature of 600° C., and thereafter was allowed to cool in the atmosphere.
A Charpy test specimen in accordance with JIS Z 2244 (2009) was prepared from the center position of a cross section perpendicular to the longitudinal direction of the round bar after the thermal refining treatment. A cross section perpendicular to the longitudinal direction of the Charpy test specimen was a square of 10 mm×10 mm, and the length was 55 mm. The notch was a U-notch shape, with the notch radius being set to 1 mm and the notch depth being set to 2 mm. The central axis of the Charpy test specimen matched the central axis of the round bar after the thermal refining treatment. A Charpy impact test was performed at normal temperature (20±15° C.) in accordance with JIS Z 2244 (2009), and impact values (J/cm2) were measured. The measurement results are shown in Table 2. If the impact value was 70 J/cm2 or more, it was determined that excellent toughness was obtained.
[Test Results]
The test results are shown in Table 2.
Referring to Table 2, in Test Numbers 1 to 9 and Test Number 25, the chemical composition was appropriate, and F1 satisfied Formula (1) and F2 satisfied Formula (2). In addition, the basicity in the LF of the secondary refining was within the range of 2.5 to 4.5. Therefore, the number of Mn sulfides was 100.0 per mm2 or less, the number of coarse Mn sulfides having an equivalent circular diameter of 3.0 μm or more was within the range of 1.0 to 10.0 per mm2, and the number of oxides was 15.0 per mm2 or less. Therefore, the average width of flank wear VB of these test numbers was 100% or less relative to the reference value (average width of flank wear VB of Test Number 24), and excellent machinability was obtained. Further, in the high temperature fatigue strength test, the fatigue strength was 420 MPa or more. In other words, in the steel material, excellent high temperature fatigue strength was obtained. In addition, in the joint high temperature fatigue strength test, the fatigue strength was 360 MPa or more. In other words, excellent high temperature fatigue strength was obtained in a HAZ also. In addition, in the toughness evaluation test, the impact value was 70 J/cm2 or more. In other words, excellent toughness was obtained in the steel material.
On the other hand, in Test Number 10, the C content was too low. Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa, and in the joint high temperature fatigue strength test, the fatigue strength was less than 360 MPa. In other words, the high temperature fatigue strength of the steel material was low, and the high temperature fatigue strength of a HAZ was also low.
In Test Number 11, the C content was too high. Therefore, the average width of flank wear VB was more than 100% relative to the reference value, and the machinability was low. In addition, in the toughness evaluation test, the impact value was less than 70 J/cm2, and the toughness of the steel material was low.
In Test Number 12, the Mo content was too low. Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa.
In Test Number 13, the Mo content was too high. Therefore, in the toughness evaluation test, the impact value was less than 70 J/cm2, and the toughness of the steel material was low.
In Test Number 14, the V content was too low. Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa.
In Test Number 15, the V content was too high. Therefore, in the toughness evaluation test, the impact value was less than 70 J/cm2, and the toughness of the steel material was low.
In Test Number 16, the F1 value was less than the lower limit of Formula (1). Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa, and the high temperature fatigue strength of the steel material was low. It is considered that, because the F1 value was less than the lower limit of Formula (1), carbides were not subjected to aging precipitation sufficiently.
In Test Number 17, the F1 value was more than the upper limit of Formula (1). Therefore, in the toughness evaluation test, the impact value was less than 70 J/cm2.
In Test Number 18 and 19, the F2 value did not satisfy Formula (2). Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa, and the high temperature fatigue strength of the steel material was low. It is considered that, because the F2 value did not satisfy Formula (2), carbides were not subjected to aging precipitation sufficiently.
In Test Number 20, the basicity in the LF during the secondary refining was too low. Therefore, the number of Mn sulfides was more than 100.0 per mm2, and the number of coarse Mn sulfides was more than 10.0 per mm2. Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa, and in the joint high temperature fatigue strength test, the fatigue strength was less than 360 MPa. In other words, the high temperature fatigue strength of the steel material was low, and the high temperature fatigue strength of a HAZ was also low.
In Test Number 21, the basicity in the LF during the secondary refining was too low. Therefore, the number of Mn sulfides was more than 100.0 per mm2, and the number of oxides was more than 15.0 per mm2. Therefore, in the high temperature fatigue strength test, the fatigue strength was less than 420 MPa, and in the joint high temperature fatigue strength test, the fatigue strength was less than 360 MPa. In other words, the high temperature fatigue strength of the steel material was low, and the high temperature fatigue strength of a HAZ was also low.
In Test Numbers 22 and 23, the basicity in the LF during the secondary refining was too high. Therefore, the number of coarse Mn sulfides was less than 1.0 per mm2. Therefore, the average width of flank wear VB was more than 100% relative to the reference value, and the machinability of the steel material was low.
An embodiment of the present invention has been described above. However, the foregoing embodiment is merely an example for implementing the present invention. Accordingly, the present invention is not limited to the above embodiment, and the above embodiment can be appropriately modified and implemented within a range which does not deviate from the gist of the present invention.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2018-104609 | May 2018 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2019/021698 | 5/31/2019 | WO |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2019/230946 | 12/5/2019 | WO | A |
| Number | Name | Date | Kind |
|---|---|---|---|
| 20040129243 | Robelet | Jul 2004 | A1 |
| 20070163687 | Kurosawa | Jul 2007 | A1 |
| 20150107544 | Lehnert et al. | Apr 2015 | A1 |
| Number | Date | Country |
|---|---|---|
| 2004181534 | Jul 2004 | JP |
| 2006037177 | Feb 2006 | JP |
| 2015078693 | Apr 2015 | JP |
| 1020060126375 | Dec 2006 | KR |
| Entry |
|---|
| Wataru et al., KR20060126375A Google Patents machine translation printed on Mar. 7, 2023, Dec. 7, 2006, entire translation (Year: 2006). |
| Number | Date | Country | |
|---|---|---|---|
| 20210230724 A1 | Jul 2021 | US |
