Steel for Induction Hardening
A steel for induction hardening according to the present invention includes a chemical composition consisting of, in mass percent: C: 0.53 to less than 0.58%, Si: 0.70 to 1.40%, Mn: 0.20 to 1.40%, P: less than 0.020%, S: 0.025% or less, Al: more than 0.06% to 0.15%, N: 0.0020 to 0.0080%, O: 0.0015% or less, B: 0.0003 to 0.0040%, Ti: 0.010 to 0.050%, and Ca: 0.0005 to 0.005%, with the balance being Fe and impurities, and satisfies Formulae (1) to (3). The steel microstructure is made up of ferrite and pearlite. A ratio of a number of composite inclusions is 20% or more. C+Si/7+Mn/5+Cr/9+Mo/2.5≤0.98 (1) C+Si/10+Mn/20+Cr/25≥0.70 (2) Cr/Si≤0.20 (3)
The present invention relates to steel, and more particularly to steel for induction hardening.
BACKGROUND ARTMachine components as represented by toothed gears are usually required to have excellent surface fatigue strengths. As a surface hardness is higher, an excellent surface fatigue strength can be obtained. For that reason, machine components required to have a surface fatigue strength may be produced by induction hardening.
An example of a method for producing such machine components is as follows. Hot forging is performed on a steel material for induction hardening to produce an intermediate product. Induction hardening is performed on the intermediate product. Grinding machining is performed on the intermediate product subjected to the induction hardening, thereby producing a machine component as represented by a toothed gear.
Techniques for improving a fatigue strength of the above machine component are proposed in Japanese Patent No. 4014042 (Patent Literature 1) and Japanese Patent No. 5742801 (Patent Literature 2).
A steel bar for induction hardening disclosed in Patent Literature 1 consists of, in mass percent, C: 0.5 to 0.7%, Si: 0.1 to 1.5%, Mn: 0.2 to 1.5%, Cr: 0 to 1.5%, V: 0 to 0.10%, S: 0.002 to 0.05%, Al: 0.01 to 0.04%, and N: 0.005 to 0.012%, with the balance being Fe and impurities, wherein, in the impurities, Ti is 0.003% or less, O is 0.0015% or less, P is 0.02% or less, and a value X represented by Formula (1) is 0.62 to 0.90. In the outer-layer region of this steel bar, a number of inclusions other than MnS is 2/mm2 or less, the inclusions each having a value A represented by Formula (2) of 0.80 or more, an aspect ratio of 3 or less, and a minor axis of 10 μm or more. Here, Formula (1) is X=C (%)+0.11×Si (%)+0.07×Mn (%)+0.08×Cr (%). Formula (2) is A=(MnMIN/MnAVE). In Formula (1), C (%), Si (%), Mn (%), and Cr (%) mean contents of respective elements (mass percent). In Formula (2), MnMIN means a lower-limit value of a concentration of Mn in an outer-layer region (mass percent), and MnAVE means an average value of the concentration of Mn (mass percent).
A hot-rolled steel bar or a hot-rolled wire rod disclosed in Patent Literature 2 has a chemical composition consists of, in mass percent, C: 0.55 to 0.75%, Si: 0.1 to 1.0%, Mn: 0.3 to 1.5%, Cr: 0.1 to 2.0%, S: 0.002 to 0.05%, Al: 0.01 to 0.2%, and N: 0.002 to 0.01%, the balance being Fe and impurities of which P and O are P: 0.025% or less and O: 0.002% or less, respectively, and making Fn1 represented by the following Formula (1) 2.5 to 4.5. In its structure, a fraction of pearlite is 90% or more, an average distance between pearlite lamellae is 150 to 300 nm, and a standard deviation of the distances between the pearlite lamellae is 25 nm or less. Formula (1) is Fn1=3Si+Mn+1.5Cr, where symbols of elements mean contents of the respective elements (mass percent).
CITATION LIST Patent Literature Patent Literature 1: Japanese Patent No. 4014042 Patent Literature 2: Japanese Patent No. 5742801 SUMMARY OF INVENTION Technical ProblemThe steel materials proposed in Patent Literature 1 and Patent Literature 2 can provide excellent surface fatigue strengths. However, it is preferable if excellent surface fatigue strengths of steel materials subjected to the induction hardening can also be provided by other methods. When a toothed gear is produced using a steel material, the toothed gear is also required to have an excellent bending fatigue strength in its dedendum. When a steel material is used to produce a machine component such as a toothed gear, the machine component is also required to have an excellent machinability.
An objective of the present invention is to provide steel for induction hardening that has an excellent machinability and provides an excellent surface fatigue strength and an excellent bending fatigue strength after induction hardening.
Solution to ProblemA steel for induction hardening according to the present invention includes a chemical composition consisting of, in mass percent: C: 0.53 to less than 0.58%, Si: 0.70 to 1.40%, Mn: 0.20 to 1.40%, P: less than 0.020%, S: 0.025% or less, Al: more than 0.06% to 0.15%, N: 0.0020 to 0.0080%, O: 0.0015% or less, B: 0.0003 to 0.0040%, Ti: 0.010 to 0.050%, Ca: 0.0005 to 0.005%, Cr: 0 to 0.15%, Cu: 0 to 0.50%, Ni: 0 to 0.30%, Mo: 0 to 0.20%, V: 0 to 0.05%, and Nb: 0 to 0.05%, with the balance being Fe and impurities, and satisfying Formulae (1) to (3). Its steel micro-structure is made up of ferrite and pearlite, where an area fraction of the pearlite is 85% or more. In the steel, a ratio of a number of composite inclusions to a total number of Al2O3 inclusions and composite inclusions is 20% or more. The composite inclusions are inclusions that contain, in mass percent, 2.0% or more of SiO2 and 2.0% or more of CaO, and the 99% or more of the balance includes Al2O3.
C+Si/7+Mn/5+Cr/9+Mo/2.5≤0.98 (1)
C+Si/10+Mn/20+Cr/25≥0.70 (2)
Cr/Si≤0.20 (3)
Here, symbols of elements in Formulae (1) to (3) are to be substituted by contents of corresponding elements (mass percent).
Advantageous Effects of InventionThe steel for induction hardening according to the present invention has an excellent machinability and provides an excellent surface fatigue strength and an excellent bending fatigue strength after induction hardening.
The present inventors conducted investigation and studies about machinability of steel for induction hardening, surface fatigue strength of steel material (machine component) subjected to induction hardening, and bending fatigue strength. Consequently, the present inventors obtained the following findings.
(1) To increase a surface fatigue strength of a steel material subjected to induction hardening, it is effective to increase a surface hardness of the steel material subjected to the induction hardening. To increase the surface hardness, it is preferable to perform induction hardening to make a micro-structure in an outer layer of the steel material a uniform hardening structure (martensite). In a case where the micro-structure in the outer layer of the steel material becomes a nonuniform structure, such as a case where ferrite or the like is left in the micro-structure in the outer layer, the surface hardness decreases, and the surface fatigue strength decreases.
To obtain a uniform hardening structure using the induction hardening, it is preferable that a micro-structure of steel for induction hardening is made up of ferrite and pearlite and an area fraction of pearlite is higher in the structure (hereafter, referred to as a fraction of pearlite).
Define Fn1 as Fn1=C+Si/7+Mn/5+Cr/9+Mo/2.5. Fn1 is an index of hardenability. Excessively high Fn1 indicates an excessively high hardenability. In this case, bainite is produced in the micro-structure of the steel for induction hardening, decreasing the fraction of pearlite. As a result, a nonuniform structure is liable to form in the outer layer even when the induction hardening is performed. When Fn1 is 0.98 or less, the micro-structure of the steel for induction hardening is made up of ferrite (pro-eutectoid ferrite) and pearlite, and the fraction of pearlite is 85% or more. “The micro-structure is made up of ferrite and pearlite” means that a total area fraction of ferrite (pro-eutectoid ferrite) and pearlite in the micro-structure is 97% or more.
(2) To obtain a uniform hardening structure using the induction hardening, it is preferable that a micro-structure of steel for induction hardening is a ferrite-pearlite micro structure and the fraction of pearlite is 85% or more as described above.
Define Fn2 as Fn2=C+Si/10+Mn/20+Cr/25. Fn2 is an index of a fraction of pearlite in a case where the micro-structure of steel is a ferrite-pearlite micro structure. The higher Fn2 is, the higher the fraction of pearlite in the micro-structure is. When Fn2 being less than 0.70, the fraction of pearlite in the micro-structure is less than 85%, and a nonuniform structure is liable to be produced in an outer layer of a steel material subjected to induction hardening. As a result, a surface fatigue strength of the steel material decreases. When Fn2 is 0.70 or more, the fraction of pearlite in the micro-structure is 85% or more.
(3) To obtain a uniform hardening structure using the induction hardening, it is further preferable that cementite in the pearlite is easily dissolved during the induction hardening. When undissolved cementite is left in a steel material subjected to the induction hardening, a nonuniform structure forms, resulting in a decrease in surface hardness of the steel material subjected to the induction hardening. As a result, a surface fatigue strength of the steel material decreases.
Si and Cr both reduce pearlite lamellar spacing, making the cementite easily dissolved in the induction hardening. In addition, Si and Cr increase a temper softening resistance of steel. Therefore, Si and Cr both inhibit formation of cementite during tempering, increasing a surface fatigue strength of a steel material. However, Cr concentrates in cementite to stabilize the cementite. Therefore, an excessively high content of Cr makes it difficult to dissolve cementite during high-frequency heating, which makes undissolved cementite easily left in a steel material subjected to the induction hardening. By decreasing a content of Cr with respect to a content of Si, it is possible to inhibit the stabilization of cementite by Cr while at the same time reducing the pearlite lamellar spacing. In this case, cementite is easily dissolved during the high-frequency heating, and the cementite resists being left after the induction hardening.
Define Fn3 as Fn3=Cr/Si. Fn3 is an index indicating how cementite is easily dissolved during the induction hardening. The lower Fn3 is, the more easily cementite in steel is dissolved in the high-frequency heating. In contrast, a high Fn3 indicates that the content of Cr is excessively high with respect to the content of Si. In this case, cementite resists being dissolved during the high-frequency heating. Consequently, a sufficient hardness is not obtained for a steel material subjected to the hardening. When Fn3 is 0.20 or less, cementite is sufficiently dissolved during the induction hardening. As a result, a sufficient surface hardness is obtained in the steel material subjected to the induction hardening, and an excellent surface fatigue strength is obtained.
(4) In addition, a surface fatigue strength of a steel material subjected to the induction hardening is affected by what inclusions in steel are. Steel for machine components produced through the induction hardening (e.g., a toothed gear) is produced by Al deoxidation. Therefore, there are Al2O3 inclusions in the steel. The Al2O3 inclusions are liable to agglomerate in a solidification process and liable to form Al2O3 inclusion groups (clusters), which are coarse. Such clusters cause a decrease in surface fatigue strength of a machine component subjected to the induction hardening. In the present specification, the Al2O3 inclusions mean inclusions containing Al2O3 at 99% or more in mass percent.
In addition, the Al2O3 inclusions have a low adhesiveness on their interfaces with matrices of steel (base metal). Therefore, gaps are likely to develop in interfaces between the Al2O3 inclusions and the matrices during plastic deformation such as hot forging. Such gaps cause a decrease in surface fatigue strength of the machine component.
Based on the above findings, the present inventors conducted investigations and studies about a method for inhibiting the agglomeration of the inclusions and increasing the adhesiveness on the matrix interfaces. Consequently, the present inventors obtained the following new findings.
In the present specification, inclusions that contain, in mass percent, 2.0% or more of SiO2 and 2.0% or more of CaO with 99% by mass of the balance being Al2O3 are defined as “composite inclusions”. The composite inclusions resist agglomerating and forming clusters. In addition, an adhesiveness of the composite inclusions on the matrix interfaces is higher than that of the Al2O3 inclusions. Therefore, by increasing a ratio of the composite inclusions to the inclusions in steel, it is possible to increase the surface fatigue strength.
In the present specification, the ratio of the number of composite inclusions to the total number of Al2O3 inclusions and composite inclusions in steel is defined as a composite-inclusion ratio Ra (%).
The higher the composite-inclusion ratio Ra is, the lower the ratio of the Al2O3 inclusions in steel is. In this case, it becomes difficult for inclusions to agglomerate, and the formation of clusters is inhibited. In addition, as described above, the adhesiveness of the composite inclusions on the matrix interfaces is high. Hence, when Al2O3 inclusions are reduced by formation of composite inclusions, a decrease in surface fatigue strength attributable to a decrease in adhesiveness between inclusions and matrices in steel is also inhibited.
When the composite-inclusion ratio Ra is 20% or more, it is possible to inhibit the formation of clusters of Al2O3 inclusions sufficiently. In addition, the adhesiveness of the matrices in steel on the inclusions is also improved. As a result, it is possible to increase a surface fatigue strength of a steel material subjected to induction hardening.
(5) To increase a bending fatigue strength of a steel material subjected to induction hardening, it is effective, in addition to the above conditions, to increase a grain boundary strength of the steel material subjected to the induction hardening. When B is contained, grain-boundary segregation of P is inhibited. Therefore, the grain boundary strength of the steel material subjected to the induction hardening is increased. As a result, the bending fatigue strength is increased.
(6) To increase a machinability of steel for induction hardening, S is contained. S combines with Mn to form binding MnS, decreasing a cutting resistance of steel. As a result, the machinability of the steel is increased. In contrast, an excessively high content of S results in a decrease in the surface fatigue strength. In the chemical composition of the steel for induction hardening according to the present embodiment, when a content of S is 0.025% or less, it is possible to increase the machinability of the steel while at the same time inhibiting the decrease in the surface fatigue strength.
To further increase the machinability of the steel, it is effective not to increase a hardness of the steel to excess. Hence, in the chemical composition of the steel for induction hardening according to the present embodiment, in addition to the specification of the content of S described above, a content of C is set at 0.53 to less than 0.58%. When the content of C is 0.53 to less than 0.58%, it is possible to increase a machinability of the steel for induction hardening while at the same time keeping the surface fatigue strength of the steel material subjected to the induction hardening.
(7) To further increase the machinability of the steel, it is effective to increase an amount of dissolved Al. When steel containing a large amount of dissolved Al is subjected to cutting work, dissolved Al forms Al oxide on a cut surface. In addition, the Al oxide is also formed on a surface of a portion of the steel material that is cut by a cutting tool. Therefore, the cut portion resists galling on the cutting tool. As a result, wear of the cutting tool is inhibited, and the machinability of the steel is increased. In the chemical composition of the steel for induction hardening according to the present invention, when a content of Al is more than 0.06% to 0.15%, it is possible to obtain Al to be used to form the Al2O3 inclusions described above as well as Al present in the steel in a form of the dissolved Al. Therefore, the machinability of the steel is increased.
The steel for induction hardening according to the present embodiment that is made based on the above findings includes a chemical composition consisting of, in mass percent: C: 0.53 to less than 0.58%, Si: 0.70 to 1.40%, Mn: 0.20 to 1.40%, P: less than 0.020%, S: 0.025% or less, Al: more than 0.06% to 0.15%, N: 0.0020 to 0.0080%, O: 0.0015% or less, B: 0.0003 to 0.0040%, Ti: 0.010 to 0.050%, Ca: 0.0005 to 0.005%, Cr: 0 to 0.15%, Cu: 0 to 0.50%, Ni: 0 to 0.30%, Mo: 0 to 0.20%, V: 0 to 0.05%, and Nb: 0 to 0.05%, with the balance being Fe and impurities, and satisfying Formulae (1) to (3). Its steel micro-structure is made up of ferrite and pearlite, where an area fraction of the pearlite is 85% or more. In the steel, a ratio of a number of composite inclusions to a total number of Al2O3 inclusions and composite inclusions is 20% or more. The composite inclusions are inclusions that contain, in mass percent, 2.0% or more of SiO2 and 2.0% or more of CaO, and the 99% or more of the balance includes Al2O3.
C+Si/7+Mn/5+Cr/9+Mo/2.5≤0.98 (1)
C+Si/10+Mn/20+Cr/25≥0.70 (2)
Cr/Si≤0.20 (3)
Here, symbols of elements in Formulae (1) to (3) are to be substituted by contents of corresponding elements (mass percent).
The above chemical composition may contain one or more types selected from the group consisting of Cr: 0.05 to 0.15%, Cu: 0.03 to 0.50%, Ni: 0.03 to 0.30%, and Mo: 0.01 to 0.20%.
The above chemical composition may contain one or two types selected from the group consisting of V: 0.01 to 0.05% and Nb: 0.01 to 0.05%.
The steel for induction hardening according to the present embodiment will be described below in detail. The sign “%” following each element means mass percent unless otherwise noted.
[Chemical Composition]
The chemical composition of the steel for induction hardening according to the present embodiment contains the following elements.
C: 0.53 to Less than 0.58%
Carbon (C) increases a surface fatigue strength of steel material subjected to the induction hardening. An excessively low content of C results in failure to provide this effect. In contrast, an excessively high content of C results in decreases in a cold workability and a machinability of the steel. Consequently, a content of C is 0.53 to less than 0.58%. A lower limit of the content of C is preferably 0.54%, more preferably 0.55%. An upper limit of the content of C is preferably 0.57%, more preferably 0.56%.
Si: 0.70 to 1.40%
Silicon (Si) deoxidizes steel. In addition, Si increases temper softening resistance and inhibits precipitation of cementite in tempering performed after the induction hardening. Moreover, Si reforms the Al2O3 inclusions to form composite inclusions (Al2O3—CaO—SiO2), which resist agglomerating. The formation of the composite inclusions increases the surface fatigue strength of the steel material subjected to the induction hardening. An excessively low content of Si results in failure to provide these effects. In contrast, an excessively high content of Si results in a decrease in cold workability of steel. Consequently, a content of Si is 0.70 to 1.40%. A lower limit of the content of Si is preferably 0.72%, more preferably 0.75%. An upper limit of the content of Si is preferably 1.38%, more preferably 1.36%.
Mn: 0.20 to 1.40%
Manganese (Mn) increases a surface fatigue strength of steel material subjected to the induction hardening. An excessively low content of Mn results in failure to provide this effect. In contrast, an excessively high content of Mn results in a decrease in cold workability of steel. In addition, an excessively high content of Mn causes segregation. As a result, grain boundary strength decreases, and a surface fatigue strength and/or a bending fatigue strength of a steel material decreases. In addition, an excessively high content of Mn may result in a decrease in machinability of steel. Consequently, a content of Mn is 0.20 to 1.40%. A lower limit of the content of Mn is preferably 0.30%, more preferably 0.35%. An upper limit of the content of Mn is preferably 1.30%, more preferably 1.25%.
P: Less than 0.020%
Phosphorus (P) is an impurity. P segregates in grain boundaries to embrittle them. Therefore, P decreases a surface fatigue strength of a steel material subjected to the induction hardening. Consequently, a content of P is less than 0.020%. An upper limit of the content of P is preferably 0.015%, more preferably 0.012%. The content of P is preferably as low as possible.
S: 0.025% or Less
Sulfur (S) is unavoidably contained. S forms inclusions (MnS), increasing a machinability of steel for induction hardening. In contrast, an excessively high content of S causes generation of coarse inclusions (MnS), decreasing a surface fatigue strength of a steel material subjected to the induction hardening. Consequently, a content of S is 0.025% or less. An upper limit of the content of S is preferably 0.024%, more preferably 0.023%. A lower limit of the content of S to increase the machinability is preferably 0.005%, more preferably 0.008%.
Al: More than 0.06% to 0.15%
Aluminum (Al) deoxidizes steel. In addition, Al combines with N in steel to form AlN, inhibiting grains from coarsening during the induction hardening. Moreover, Al is present in steel in a form of dissolved Al. In cutting working, the dissolved Al is exposed on a cut surface of a steel material, forming Al oxide. The Al oxide is also formed on a surface of a portion of the steel material cut by a cutting tool. Therefore, the cut portion resists galling on the cutting tool. As a result, wear of the tool is inhibited, and a machinability of steel is increased. An excessively low content of Al results in failure to provide these effects. In contrast, an excessively high content of Al causes formation of a large number of coarse Al2O3 inclusions and Al2O3 clusters, aggregates of a plurality of Al2O3 inclusions, resulting in a decrease in a surface fatigue strength of a steel material subjected to the induction hardening. Consequently, a content of Al is more than 0.06% to 0.15%. A lower limit of the content of Al is preferably 0.08%, more preferably 0.085%, still more preferably 0.09%. An upper limit of the content of Al is preferably 0.14%, more preferably 0.13%. The content of Al used herein means a content of Al in total.
N: 0.0020 to 0.0080%
Nitrogen (N) combines with Al to form AlN, inhibiting grains from coarsening during the induction hardening. As a result, N increases a surface fatigue strength of a steel material subjected to the induction hardening. An excessively low content of N results in failure to provide this effect. In contrast, an excessively high content of N causes N to be dissolved in ferrite to excess, bringing about strain aging, which results in a decrease in cold workability of steel. In addition, an excessively high content of N causes formation of coarse nitride, resulting in a decrease in a surface fatigue strength of a steel material. Consequently, a content of N is 0.0020 to 0.0080%. A lower limit of the content of N is preferably 0.0025%, more preferably 0.0030%. An upper limit of the content of N is preferably 0.0075%, more preferably 0.0070%.
O: 0.0015% or Less
Oxygen (O) is an impurity. O combines with Al, Si, and Ca to form their oxides (or their oxide inclusions), resulting in a decrease in a surface fatigue strength of a steel material subjected to the induction hardening. Consequently, a content of O is 0.0015% or less. An upper limit of the content of O is preferably 0.0014%, more preferably 0.0013%. The content of O is preferably as low as possible.
B: 0.0003 to 0.0040%
Boron (B) is dissolved in steel, increasing a hardenability of steel. As a result, B increases a surface fatigue strength of a steel material subjected to the induction hardening. In addition, B increases grain boundary strength, increasing a bending fatigue strength of a steel material subjected to the induction hardening. An excessively low content of B results in failure to provide the effects described above effectively. In contrast, an excessively high content of B makes the above effects saturated. Consequently, a content of B is 0.0003 to 0.0040%. A lower limit of the content of B is preferably 0.0005%, more preferably 0.0008%. An upper limit of the content of B is preferably 0.0038%, more preferably 0.0036%.
Ti: 0.010 to 0.050%
Titanium (Ti) forms Ti nitride or Ti carbide, inhibiting grains from coarsening during the induction hardening. As a result, a surface fatigue strength and bending fatigue strength of a steel material subjected to the induction hardening are increased. In addition, Ti combines with N, thereby inhibiting B from combining with N to secure an amount of dissolved B. An excessively low content of Ti results in failure to provide the effects described above. In contrast, an excessively high content of Ti causes formation of coarse Ti nitride and Ti carbide, resulting in a decrease in cold workability of steel. Consequently, a content of Ti is 0.010 to 0.050%. A lower limit of the content of Ti is 0.012%, more preferably 0.013%. An upper limit of the content of Ti is preferably 0.048%, more preferably 0.046%.
Ca: 0.0005 to 0.005%
Calcium (Ca) reforms Al2O3 inclusions to form composite inclusions (Al2O3—CaO—SiO2). Reforming the Al2O3 inclusions to form the composite inclusions increases a surface fatigue strength of a steel material subjected to the induction hardening. An excessively low content of Ca results in failure to provide this effect. In contrast, an excessively high content of Ca causes coarse inclusions to increase, resulting instead in a decrease in the surface fatigue strength of the steel material subjected to the induction hardening. Consequently, a content of Ca is 0.0005 to 0.005%. A lower limit of the content of Ca is preferably 0.0008%, more preferably 0.0010%. An upper limit of the content of Ca is preferably 0.0048%, more preferably 0.0046%.
The balance of the chemical composition of the steel for induction hardening according to the present embodiment is Fe and impurities. Here, the impurities mean elements that are mixed from ores and scraps used as raw material, a producing environment, or the like when the steel for induction hardening is produced in an industrial manner, and are allowed to be mixed within ranges in which the impurities have no adverse effect on the steel for induction hardening according to the present embodiment.
The steel for induction hardening according to the present embodiment may further contain one or more types selected from the group consisting of Cr, Cu, Ni, and Mo. These elements all increase a surface fatigue strength of a steel material subjected to the induction hardening.
Cr: 0 to 0.15%
Chromium (Cr) is an optional element and need not be contained. When contained, Cr is dissolved in steel, increasing a surface fatigue strength of a steel material subjected to the induction hardening. In addition, Cr increases a temper softening resistance of steel and inhibits formation of cementite during tempering. As a result, a surface fatigue strength of a steel material increases. Even a trace amount of Cr can provide the above effect to some extent. In contrast, Cr is likely to concentrate in cementite to stabilize the cementite. When cementite is stabilized, the cementite resists being dissolved during the induction hardening, and the cementite may be left in some cases. Therefore, dissolved C is not obtained sufficiently, and a sufficient hardness of a steel material is not obtained. As a result, a surface fatigue strength of the steel material decreases. Consequently, a content of Cr is 0 to 0.15%. To obtain the above effect more effectively, a lower limit of the content of Cr is preferably 0.01%, more preferably 0.05%, still more preferably 0.06%, still more preferably 0.07%. An upper limit of the content of Cr is preferably 0.14%, more preferably 0.13%.
Cu: 0 to 0.50%
Copper (Cu) is an optional element and need not be contained. When contained, Cu is dissolved in steel, increasing a surface fatigue strength of a steel material subjected to the induction hardening. Even a trace amount of Cu can provide this effect to some extent. In contrast, an excessively high content of Cu makes the above effect saturated. Consequently, a content of Cu is 0 to 0.50%. In order to obtain the above effect more effectively, a lower limit of the content of Cu is preferably 0.03%, more preferably 0.04%. An upper limit of the content of Cu is preferably 0.45%, more preferably 0.40%.
Ni: 0 to 0.30%
Nickel (Ni) is an optional element and need not be contained. When contained, Ni is dissolved in steel, increasing a surface fatigue strength of a steel material subjected to the induction hardening. Even a trace amount of Ni can provide the above effect to some extent. In contrast, an excessively high content of Ni makes the above effect saturated. Consequently, a content of Ni is 0 to 0.30%. In order to obtain the above effect more effectively, a lower limit of the content of Ni is preferably 0.03%, more preferably 0.04%. An upper limit of the content of Ni is preferably 0.25%, more preferably 0.20%.
Mo: 0 to 0.20%
Molybdenum (Mo) is an optional element and need not be contained. When contained, Mo is dissolved in steel, increasing a surface fatigue strength of a steel material subjected to the induction hardening. Even a trace amount of Mo can provide the above effect to some extent. In contrast, an excessively high content of Mo makes a ratio of pearlite in a steel material for induction hardening less than 85%, resulting in a decrease in cold workability. Consequently, a content of Mo is 0 to 0.20%. In order to obtain the above effect more effectively, a lower limit of the content of Mo is preferably 0.01%, more preferably 0.02%. An upper limit of the content of Mo is preferably 0.18%, more preferably 0.16%.
The steel for induction hardening according to the present embodiment may further contain, in lieu of part of Fe, one or more types selected from the group consisting of V and Nb. These elements both increase a surface fatigue strength and a bending fatigue strength of a steel material.
V: 0 to 0.05%
Vanadium (V) is an optional element and need not be contained. When contained, V forms V nitride, V carbide, and V carbo-nitride, inhibiting grains from coarsening during the induction hardening. As a result, a surface fatigue strength and bending fatigue strength of a steel material subjected to the induction hardening are increased. Even a trace amount of V can provide the above effect to some extent. In contrast, an excessively high content of V causes formation of coarse V precipitate, resulting in a decrease in cold workability of steel. Consequently, a content of V is 0 to 0.05%. A lower limit of the content of V is preferably 0.01%, more preferably 0.02%, still more preferably 0.025%, still more preferably 0.03%. An upper limit of the content of V is preferably 0.045%, more preferably 0.04%.
Nb: 0 to 0.05%
Niobium (Nb) is an optional element and need not be contained. When contained, Nb forms Nb nitride, Nb carbide, and Nb carbo-nitride, inhibiting grains from coarsening during the induction hardening. As a result, a surface fatigue strength and bending fatigue strength of a steel material subjected to the induction hardening are increased. Even a trace amount of Nb can provide the above effect to some extent. In contrast, an excessively high content of Nb causes formation of coarse Nb precipitate, resulting in a decrease in cold workability of steel. Consequently, a content of Nb is 0 to 0.05%. In order to obtain the above effect more effectively, a lower limit of the content of Nb is preferably 0.01%, more preferably 0.012%. An upper limit of the content of Nb is preferably 0.048%, more preferably 0.046%.
[Formula (1)]
The above chemical composition further satisfies Formula (1):
C+Si/7+Mn/5+Cr/9+Mo/2.5≤0.98 (1)
where, symbols of elements in Formula (1) are to be substituted by contents of the corresponding elements (in mass percent).
Define Fn1 as Fn1=C+Si/7+Mn/5+Cr/9+Mo/2.5. Fn1 is an index of hardenability. Fn1 being more than 1.05 indicates an excessively high hardenability. In this case, hard bainite is produced in part of a micro-structure of rolled steel for induction hardening. Therefore, a ferrite-pearlite micro structure is not obtained. When Fn1 is 1.05 or less, a micro-structure of steel for induction hardening is a ferrite-pearlite microstructure. However, when Fn1 is more than 0.98, a sufficient machinability is not obtained. Consequently, Fn1 is set at 0.98 or less. In this case, a micro-structure of steel for induction hardening is a ferrite-pearlite microstructure, and in addition, a sufficient machinability is also obtained. An upper limit of Fn1 is preferably 0.97. In order to obtain a hardenability, a lower limit of Fn1 is preferably 0.72.
[Formula (2)]
The above chemical composition further satisfies Formula (2):
C+Si/10+Mn/20+Cr/25≥0.70 (2)
where, symbols of elements in Formula (2) are to be substituted by contents of corresponding elements (in mass percent).
Define Fn2 as Fn2=C+Si/10+Mn/20+Cr/25. Fn2 is an index of a fraction of pearlite in a case where the micro-structure of steel is a ferrite-pearlite microstructure. The higher Fn2 is, the higher the fraction of pearlite in the micro-structure is. When Fn2 is less than 0.70, the fraction of pearlite in the micro-structure is less than 85%. When Fn2 is 0.70 or more, the fraction of pearlite in the micro-structure is 85% or more. A lower limit of Fn2 is preferably 0.72.
[Formula (3)]
The above chemical composition further satisfies Formula (3):
Cr/Si≤0.20 (3)
where, symbols of elements in Formula (3) are to be substituted by contents of corresponding elements (mass percent).
As described above, Si and Cr both reduce pearlite lamellar spacing. When the pearlite lamellar spacing is reduced, cementite is easily dissolved during the induction hardening. However, Cr concentrates in cementite to stabilize the cementite. By increasing a content of Si with respect to a content of Cr, it is possible to inhibit the stabilization of cementite by Cr while at the same time reducing the pearlite lamellar spacing. Therefore, cementite is easily dissolved during the induction hardening, and the cementite resists being left after the induction hardening.
Define Fn3 as Fn3=Cr/Si. Fn3 is an index indicating to what degree cementite is dissolved after the induction hardening. The lower Fn3 is, the more easily cementite in steel is dissolved in the high-frequency heating. In contrast, a high Fn3 indicates that the content of Cr is excessively high with respect to the content of Si. In this case, cementite resists being dissolved during the high-frequency heating. As a result, cementite is left in a steel material subjected to the hardening, resulting in a decrease in a surface fatigue strength of the steel material subjected to the induction hardening. When Fn3 is 0.20 or less, cementite is sufficiently dissolved after the induction hardening. As a result, a sufficient hardness is obtained in the steel material subjected to the induction hardening, and an excellent surface fatigue strength is obtained. A lower limit of Fn3 is preferably 0.18.
[Micro-Structure of Steel]
When steel for induction hardening includes the above chemical composition and satisfies Formulae (1) to (3), its micro-structure is made up of ferrite (pro-eutectoid ferrite) and pearlite. That is, the micro-structure of the steel for induction hardening according to the present embodiment is a ferrite-pearlite microstructure. “The micro-structure is made up of ferrite and pearlite” herein means that a total area fraction of the ferrite and the pearlite in the micro-structure is 97% or more. In the micro-structure of the steel for induction hardening, it is preferable that the total area fraction of the ferrite and the pearlite is 100%. When the total area fraction of the ferrite and the pearlite is not 100%, the balance of the micro-structure, other than the ferrite and the pearlite, is bainite, for example. The area fraction of the pearlite in the micro-structure is defined as a fraction of pearlite (%). In the micro-structure of the steel for induction hardening according to the present embodiment, the fraction of pearlite is 85% or more.
The total area fraction of the ferrite and the pearlite in the micro-structure and the fraction of pearlite are measured by the following method. A sample is taken from the steel for induction hardening. When the steel for induction hardening is a steel bar or a wire rod, the sample is taken from a cross-sectional area of the steel bar or the wire rod (a surface perpendicular to its axis direction) of half a radius R connecting a surface and a center axis of the steel bar or the wire rod (hereafter referred to as an R/2 portion). Of surfaces of the taken sample, one perpendicular to a rolling direction of the steel material is determined as an observation surface. The observation surface is polished and thereafter etched with 3% nitric acid and alcohol (Nital etching reagent). The etched observed surface is observed under an optical microscope with 500× magnification, and photographic images of any five visual fields on the etched observed surface are created. A size of each visual field is set at 200 μm×200 μm.
In each of the visual fields, phases including ferrite, pearlite, and the like have their own different contrasts. Therefore, the phases are identified based on their respective contrasts. Of the identified phases, a total area of ferrite (μm2) and a total area of pearlite (μm2) are determined in each visual field. A ratio of a sum of a total area of ferrite and a total area of pearlite in all the visual fields to a total area of all the visual fields is defined as a total area fraction of ferrite and pearlite (%). In addition, the total area of pearlite in all the visual field to the total area of all the visual fields is defined as a fraction of pearlite (%).
[Composite-Inclusions Ratio Ra]
The steel for induction hardening according to the present embodiment contains Al2O3 inclusions and composite inclusions. In the present specification, as described above, inclusions that contain 2.0% or more of SiO2 and 2.0% or more of CaO with 99% or more of the balance being Al2O3 are defined as “composite inclusions”. An upper limit of SiO2 contained in the composite inclusions is, for example, 15%, and an upper limit of CaO contained in the composite inclusions is, for example, 25%.
In the present specification, the ratio of the number of composite inclusions to the total number of Al2O3 inclusions and composite inclusions is defined as the composite-inclusion ratio Ra (%). The higher the composite-inclusion ratio Ra is, the less the Al2O3 inclusions in steel are. In this case, it becomes difficult for Al2O3 inclusions agglomerate, and the formation of clusters is inhibited. In addition, as described above, the adhesiveness of the Al2O3 inclusions on the matrix interfaces is low, whereas the adhesiveness of the composite inclusions on the matrix interfaces is high. Hence, when a number of Al2O3 inclusions is reduced by formation of composite inclusions, a decrease in surface fatigue strength attributable to a decrease in adhesiveness between inclusions and matrices in steel is also inhibited.
When the composite-inclusion ratio Ra is 20% or more, it is possible to inhibit the formation of clusters of Al2O3 inclusions sufficiently. In addition, the adhesiveness of the matrices in steel on the inclusions is also improved. As a result, it is possible to increase a surface fatigue strength of a steel material subjected to induction hardening.
Identification of Al2O3 inclusions and composite inclusions in steel and measurement of the composite-inclusion ratio Ra can be performed by the following method. A sample is taken from a desired location in the steel for induction hardening. When the steel for induction hardening is a steel bar or a wire rod, the sample is taken from an R/2 portion of the steel bar or the wire rod. On a cross section (surface) of the R/2 portion in the sample, randomly selected 20 visual fields (with an evaluation area per visual field is 100 μm×100 μm) are observed at 1000× magnification under a scanning electron microscope (SEM).
In each visual field (referred to as an observation surface), inclusions are identified. For each of the identified inclusions, Al2O3 inclusions and composite inclusions are identified using the Energy Dispersive X-ray Spectroscopy (EDX). Specifically, when elemental analysis of the identified inclusions shows that when a content of Al and a content of O are 99% or more in mass percent, the inclusions are defined as Al2O3 inclusions. When the elemental analysis shows that the identified inclusions contain 2.0% or more of SiO2 and 2.0% or more of CaO, with the balance being substantially Al2O3 and impurities (specifically, 99% or more of the balance is Al2O3), the inclusions are defined as “composite inclusions”.
The inclusions to be identified are assumed to be inclusions having a circle equivalent diameter of 10 μm or more. Here, the circle equivalent diameter means a diameter of a circle into which an inclusion is converted and that has the same area as the inclusion.
Inclusions each having a circle equivalent diameter twice or larger a beam diameter of the EDX allows an accuracy of the elementary analysis to be increased. In the present embodiment, a beam diameter of the EDX used to identify the inclusions is assumed to be 5 μm. In this case, inclusions each having a circle equivalent diameter of less than 10 μm cannot increase an accuracy of the elementary analysis by the EDX. In addition, the inclusions each having a circle equivalent diameter of less than 10 μm have a very minor adverse on the fatigue strength. Therefore, in the present embodiment, Al2O3 inclusions and composite inclusions each having a circle equivalent diameter of 10 μm or more are assumed to be measured. The upper limit of the circle equivalent diameters of the Al2O3 inclusions and composite inclusions is not limited to particular one but, for example, 200 μm.
A total number TN1 of identified Al2O3 inclusions each having a circle equivalent diameter of 10 μm or more in all of 20 visual fields is determined. Similarly, a total number TN2 of identified composite inclusions each having a circle equivalent diameter of 10 μm or more is determined. Based on the determined total numbers, the composite-inclusion ratio Ra (%) is determined by the following Formula:
Ra=TN2/(TN1+TN2)×100
When inclusions having the same composition are adjacent to each other, and a shortest distance between the adjacent inclusions is less than 1 μm, these inclusions are regarded as one inclusion.
[Producing Method]
Description will be made about an example of a producing method of the steel for induction hardening according to the present embodiment. In the present embodiment, as an example of the steel for induction hardening, a method for producing a steel bar and a wire rod will be described. However, the steel for induction hardening according to the present embodiment is not limited to the steel bar or the wire rod.
The example of the producing method includes a steelmaking step of refining molten steel and casting the molten steel to produce a starting material (cast piece or ingot), and a hot working step of performing hot working on the starting material to produce the steel for induction hardening. Each of the steps will be described below.
[Steelmaking Step]
The steelmaking step includes a refining step and a casting step.
[Refining Step]
In the refining step, molten iron produced by a well-known method is first subjected to refining in a converter (first refining). Molten steel tapped from the converter is subjected to second refining. In the second refining, alloying elements for adjustment of components is added to produce molten steel satisfying the above chemical composition.
Specifically, Al is added to the molten steel tapped from the converter to perform deoxidation treatment. After the deoxidation treatment, slag-off treatment is performed. After the slag-off treatment, the second refining is performed. In the second refining, for example, composite refining is performed. For example, a refining treatment including LF (Ladle Furnace) or VAD (Vacuum Arc Degassing) is first performed. In addition, RH (Ruhrstahl-Hausen) vacuum degassing treatment is performed. Thereafter, final adjustment of alloy elements other than Si and Ca is performed.
After performing the second refining to perform adjustment of components of the molten steel other than Si and Ca, the molten steel is subjected to the next treatment (a heating retaining step and a final component adjusting step).
[Heating Retaining Step]
The molten steel in a ladle after the second refining (final component adjustment) is heated at a temperature of 1500 to 1600° C. for a retention time ts twice or longer than a mixing time τ(s), which is calculated by the following Formulae:
τ=800×ε−0.4
ε=((6.18×Vg×T1)/M1)ln(1+(h0/(1.46×10−5×P0)))
where, Vg: gas flow rate (Nm3/min), M1: mass of the molten steel in the ladle (ton), T1: temperature of the molten steel (K), h0: gas injection depth (m), P0: surface pressure of the molten steel (Pa), ε: agitation power density (W/ton), and τ: mixing time (s).
When the retention time ts is less than twice the mixing time c, Al2O3 inclusions are not reformed into composite inclusions sufficiently. That is, the composite-inclusion ratio Ra becomes as low as less than 20%. When the retention time ts is twice or longer than the mixing time c, the composite-inclusion ratio Ra becomes 20% or more on an assumption that other conditions are met.
[Final Component Adjusting Step]
Si and Ca are added to the molten steel subjected to the heating retaining step to produce the molten steel satisfying the chemical composition and Formulae (1) to (3) described above. Si and Ca may be each added to the molten steel as a separate raw material. Si—Ca alloy may be added to the molten steel.
The addition of Si and Ca to the molten steel that has been sufficiently, uniformly heated in the heating retaining step allows the Al2O3 inclusions to be reformed into the composite inclusions easily. By performing the final component adjusting step after the above heating retaining step, it is possible to make the composite-inclusion ratio Ra in the steel for induction hardening 20% or more.
If Si is added to the molten steel prior to the addition of Al, the composite inclusions resist forming. By adding Si and Ca to the molten steel in which Al2O3 inclusions are present, composite inclusions are formed by the Al2O3 inclusions reformed into the composite inclusions. Therefore, in the present embodiment, Al is added to the molten steel before Si and Ca are added. An order of the adding of Si and Ca is not limited to particular one. Si and Ca may be added at the same time. One of Si and Ca may be added prior to the other.
[Casting Step]
Using the molten steel produced by the above refining step, the starting material (cast piece or ingot) is produced. Specifically, the continuous casting process is performed using the molten steel to produce a cast piece. Alternatively, the ingot-making process may be performed using the molten steel to produce an ingot.
[Hot Working Step]
The produced starting material is subjected to hot working to be produced into a steel material for induction hardening (steel bar or wire rod). In the hot working process, the hot working is performed normally one or a plurality of times. When the hot working is performed a plurality of times, the hot working of the first time is, for example, blooming or hot forging, and the hot working of the next time is finish rolling using a continuous mill. In the continuous mill, horizontal stands and vertical stands are arranged alternately in a row, the horizontal stands each including a pair of horizontal rolls, the vertical stands each including a pair of vertical rolls. The steel material for induction hardening subjected to the finish rolling is cooled to room temperature. At that time, an average cooling rate of a surface temperature of the steel material for induction hardening until the surface temperature reaches 800 to 500° C. is set at 1° C./sec or less. If the average cooling rate is more than 1° C./sec, bainite is produced at 3% or more in terms of area fraction in a micro-structure of the cooled steel material for induction hardening. When the average cooling rate is 1° C./sec or less, the micro-structure of the cooled steel material for induction hardening is made up of ferrite and pearlite. A lower limit of the average cooling rate is preferably 0.1° C./sec. An upper limit of the average cooling rate is preferably 0.7° C./sec.
Through the steps described above, the steel for induction hardening according to the present embodiment can be produced.
[Method for Producing Machine Component]
The steel for induction hardening described above is produced into a machine component as represented by a toothed gear. An example of a method for producing the machine component is as follows.
First, hot forging is performed on a prepared steel material for induction hardening to produce an intermediate product. As necessary, stress relief annealing is performed on the intermediate product. The intermediate product subjected to the hot forging or the stress relief annealing is subjected to cutting working to be produced into a crude product. In a case where the machine component is a toothed gear, the crude product has a rough shape of the toothed gear. The crude product is subjected to induction hardening. After the induction hardening, grinding machining is performed to produce the machine component as represented by a toothed gear.
The steel for induction hardening according to the present embodiment satisfies the above Formulae (1) to (3) and further makes the composite-inclusion ratio Ra 20% or more. Therefore, it is possible to increase a machinability of the steel for induction hardening and further increase a surface fatigue strength and a bending fatigue strength of a machine component subjected to the induction hardening.
EXAMPLESMolten steels having chemical compositions shown in Table 1 were produced.
Each of signs “-” in Table 1 means that a content of a corresponding element is at an impurity level. Specifically, a sign “-” seen in a content of B means that the content of B is less than 0.0001%. A sign “-” seen in a content of Ti means that the content of Ti is less than 0.001%. A sign “-” seen in a content of Ca means that the content of Ca is less than 0.0001%. Signs “-” seen in contents of Cr, Cu, Ni, and Mo, respectively, mean that the contents of the corresponding elements are less than 0.01%. Signs “-” seen in contents of V mean that the contents of V are less than 0.001%. Signs “-” seen in contents of Nb mean that the contents of Nb are less than 0.001%.
In “Fn1” columns of Table 1, values of Fn1 of steels of corresponding test numbers are written. In “Fn2” columns, values of Fn2 of steels of corresponding test numbers are written. In “Fn3” columns, values of Fn3 of steels of corresponding test numbers are written.
The molten steel of the corresponding test numbers were produced by the following method. Molten irons produced by a well-known method were subjected to the first refining in a converter in the same conditions.
The molten steels other than that of a test number 40 were tapped from the converter, then subjected to the deoxidation treatment by adding Al, and thereafter subjected to the slag-off treatment. The slag-off treatment was followed by the refining treatment using VAD and then the RH vacuum degassing treatment. Through the above steps, composition components of the alloying element other than Si and Ca were adjusted.
Subsequently, the heating retaining step was performed. Ratios (ts/τ) of retention times ts of corresponding test numbers to the mixing time τ were those shown in Table 1. After the heat retention process, Si—Ca alloy was added to the molten steels other than that of the test number 40 to adjust their contents of Si and their content of Ca, and the molten steels having the chemical compositions shown in Table 1 were produced.
In contrast, for molten steel of the test number 40, deoxidation treatment by adding Si was performed after tapping of the molten steel from the converter. The subsequent processes performed on the molten steel up to the heating retaining step were the same as those performed on the molten steel of the test numbers 1 to 39 and 41. After the heating retaining step, Al and Ca were added, and the molten steel having its chemical composition shown in Table 1 was produced.
The molten steel of the test numbers 1 to 41 were used to produce cast pieces by the continuous casting process, the cast pieces each having a cross section of 400 mm×300 mm.
The produced cast pieces were heated to 1250° C. The heated cast pieces were used to be produced into billets by the blooming, the billets each having a cross section of 162 mm×162 mm. The produced billets were subjected to air cooling to a normal temperature (25° C.). The billets were heated again to 1200° C. The heated billets were subjected to the hot rolling using a continuous mill (the finish rolling) and then cooled to be produced into steel bars for induction hardening each having a diameter of 70 mm.
For each of the test numbers, an average cooling rate of a surface temperature of the corresponding steel bar subjected to the finish rolling until the surface temperature reached 800 to 500° C. is shown in Table 1. In a “cooling rate” column of Table 1, “S” (Slow) means that an average cooling rate of a surface temperature of a steel bar subjected to finish rolling corresponding to a test number until the surface temperature reached to 800 to 500° C. was 1° C./sec or less. In a “cooling rate” column of Table 1, “F” (Fast) means that an average cooling rate of a surface temperature of a steel bar subjected to finish rolling corresponding to a test number until the surface temperature reached to 800 to 500° C. was more than 1° C./sec. For each test number, a chemical composition of a produced steel bar corresponding thereto was measured. As a result, the chemical composition of the steel bar corresponding to each test number was as shown in Table 1.
[Micro-Structure Observation]
From an R/2 portion of a steel bar of each test number, a test specimen for micro-structure observation was taken. Of the surfaces of the test specimen, a cross section extending in parallel to a longitudinal direction of the steel bar (i.e., its rolling direction or its elongating direction) was defined as an observation surface. Based on the method described above, a total area fraction of ferrite and pearlite (%) was determined. A micro-structure having a total area fraction of 97% or more is shown as “F+P” in Table 2. In contrast, a micro-structure having a total area fraction of less than 97% and observed that bainite is present in the balance is shown as “F+P+B” in Table 2.
In addition, on the observation surface described above, its fraction of pearlite (%) was determined by the method described above. Results of the determination are shown in Table 2.
[Composite-Inclusions Ratio Ra]
On the steel bars for induction hardening, their composite-inclusion ratios Ra (%) were measured by the method described above. Al2O3 inclusions and composite inclusions each having a circle equivalent diameter of 10 μm or more were identified, and their composite-inclusion ratios Ra (%) were determined by the method described above. Results of the determination are shown in Table 2.
[Evaluation Test]
[Making Surface Fatigue Strength Test Specimen and Ono Type Rotating Bending Fatigue Strength Smooth Test Specimen]
A surface fatigue strength test specimen and an Ono type rotating bending fatigue strength smooth test specimen (hereafter, simply referred to as a bending fatigue strength test specimen) each simulating a machine component were made by the following method. For each test number, a steel bar was heated at 1200° C. for 30 minutes. Next, the steel bar was subjected to hot forging with a finishing temperature set at 950° C. or more to be produced into a round bar having a diameter of 35 mm. The round bar having a diameter of 35 mm was machined into the surface fatigue strength test specimen in a form of a small roller specimen. Specifically, small roller specimens for a roller-pitting test illustrated in
In addition, the round bar having a diameter of 35 mm was machined into a plurality of bending fatigue strength test specimens illustrated in
Each of the made test specimens was subjected to induction hardening. Specifically, a peripheral surface FP of the small roller specimen (a portion having a diameter of 26 mm) was subjected to the induction hardening treatment using an induction hardening apparatus with 20 kW output and 50 kHz frequency and for a heating time adjusted within a range of 5 to 10 seconds such that its hardened layer depth becomes 1.5 mm. At that time, a heating temperature of a surface of the small roller specimen was 900 to 1100° C. Thereafter, an ordinary heat treatment furnace was used to perform tempering at 160° C. for one hour. In addition, a parallel portion of a bending fatigue strength test specimen was subjected to induction hardening in the same conditions as those for the small roller specimen, and then tempered by an ordinary heat treatment furnace in the same conditions as those for the small roller specimen.
[Vickers Hardness Test]
After the induction hardening, for each test number, the peripheral surface FP (portion having a diameter of 26 mm) of the corresponding small roller specimen and the parallel portion of the corresponding bending fatigue strength test specimen were measured in Vickers hardness. Specifically, a Vickers hardness test conforming to JIS Z 2244(2009) was performed at desired three points on each of the peripheral surface FP of the small roller specimen and a surface of the parallel portion of the bending fatigue strength test specimen. At this point, a test force was set at 9.8 N.
An average value of resulting Vickers hardnesses was defined as a Vickers hardness (HV) of the each test number. An average value of Vickers hardnesses obtained from the bending fatigue strength test specimen was the same as an average value of Vickers hardnesses obtained from the small roller specimen. Therefore, the average value of the measurement results from the small roller specimen was determined as the Vickers hardness after the induction hardening. The measurement results are shown in Table 2.
[Surface Fatigue Strength Test]
The roller-pitting test was performed to determine surface fatigue strengths. The roller-pitting test was performed in a form of combination of the above small roller specimen and a large roller specimen.
Test machine: Roller-pitting test machine
Test specimens: Small roller specimen (26 mm in diameter),
Large roller specimen (130 mm in diameter), Contact portion of 150 mmR
Maximum surface pressure: 3600 MPa
Number of tests: 6
Slip Factor: −40%
Rotational speed of small roller: 2000 rpm
Peripheral speed: small roller: 2.72 m/s, large roller: 3.81 m/s
Lubricant temperature: 90° C.
Oil used: Oil for automatic transmissions
For each test number, a number of tests was six in the roller-pitting test. After the test, S—N curves with its ordinate representing interfacial pressure and its abscissa representing number of repetitions until occurrence of pitting were created. For the test number, a highest of interfacial pressures at which pitting did not occur until a number of repetitions of 2.0×107 was determined as its surface fatigue strength. A case where a largest of damaged spots on a surface of the small roller specimen had an area of 1 mm2 or more was determined as the occurrence of pitting.
Table 2 shows surface fatigue strengths resulting from the test. For the surface fatigue strengths in Table 2, a surface fatigue strength of the test number 21 was used as a reference value (100%). A surface fatigue strength of each test number is shown in a form of a ratio to the reference value (%). A surface fatigue strength of 100% or more was determined that an excellent surface fatigue strength was obtained.
[Bending Fatigue Strength Test]
The Ono type rotating bending fatigue strength test was conducted using the bending fatigue strength test specimen described above, and bending fatigue strengths were determined.
For each test number, a number of tests was seven in the Ono type rotating bending fatigue strength test. The fatigue test was conducted in a room temperature air atmosphere, and S—N curves with its ordinate representing load stress and its abscissa representing number of repetitions until occurrence of breakage were created. For the test number, a highest of load stresses at which breakage did not occur until a number of repetitions of 1.0×107 was determined as its bending fatigue strength.
Table 2 shows bending fatigue strengths resulting from the test. For the bending fatigue strengths in Table 2, a bending fatigue strength of the test number 21 was used as a reference value (100%). A bending fatigue strength of each test number is shown in a form of a ratio to the reference value (%). A bending fatigue strength of 115% or more was determined that an excellent bending fatigue strength was obtained.
[Making Machinability Evaluation Test Specimen]
A machinability evaluation test specimen was made by the following method. As with the surface fatigue strength test specimen, for each test number, a steel bar was heated at 1200° C. for 30 minutes. Next, the heated steel bar was subjected to hot forging to be produced into a round bar having a diameter of 35 mm. A finishing temperature of the hot forging was 950° C. or more. The round bar produced by the hot forging was machined to be finished into disc-shaped test specimens each having a diameter of 30 mm and a height of 15 mm (hereafter, referred to as machinability test specimens).
[Machinability Evaluation Test]
The made machinability test specimens were subjected to machinability evaluation test by drill machining. Specifically, the drill machining was performed at a constant cutting speed until a total depth of machined holes reached 1000 mm. When the machined hole depth reached 1000 mm, the drill machining was once stopped. Then, the cutting speed was set to a higher one, and the drill machining was performed again at the set cutting speed until the total depth of the machined holes reached 1000 mm. Similarly, the drill machining was performed consecutively while the cutting speed is increased, to determine a maximum cutting speed (m/min) at which the total depth of the machined holes could reach 1000 mm or more. The maximum cutting speed is usually used as an evaluation index of a tool life, and the higher the maximum cutting speed, the better the tool life is determined to be. For each of the test number, its maximum cutting speed was determined.
Conditions of the drill machining in the machinability evaluation test were as follows, where water-soluble cutting oil was used during the drill machining.
Cutting drill: φ3 mm high-speed drill
Cutting speed: 10 to 90 m/min
Feed: 0.25 mm/rev
Table 2 shows machinability evaluation resulting from the test. For the machinability evaluations in Table 2, a machinability evaluation of the test number 21 was used as a reference value (100%). A machinability evaluation of each test number is shown in a form of a ratio to the reference value (%). A maximum cutting speed of 135% or more was determined that an excellent machinability was obtained.
[Results of Evaluation]
Referring to Table 1 and Table 2, as to the steel of the test numbers 1 to 20, their chemical compositions were appropriate and satisfied Formulae (1) to (3). In addition, the producing conditions in the refining step were appropriate. Therefore, their micro-structures were ferrite-pearlite micro structures, and their fractions of pearlite were 85% or more. In addition, their composite-inclusion ratios Ra were 20% or more. In addition, their Vickers hardnesses were 730 HV or more. As a result, their surface fatigue strengths were 100% or more, indicating that excellent surface fatigue strengths were obtained. Furthermore, their bending fatigue strengths were 115% or more, indicating that excellent bending fatigue strengths were obtained. Furthermore, their machinabilities were 135% or more, indicating that excellent machinabilities were obtained.
In contrast, as to the test number 22, its content of Si was excessively low. Accordingly, its Al2O3 inclusions cannot be reformed into composite inclusions sufficiently, and its composite-inclusion ratio Ra was less than 20%. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test number 23, its content of Mn was excessively high. Therefore, bainite is produced in its microstructure after the rolling, and its fraction of pearlite was less than 85%. As a result, a Vickers hardness of its steel material subjected to the induction hardening was less than 730 HV. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. Furthermore, its machinability was less than 135%, indicating that an excellent machinability was not obtained.
As to the test number 24, its content of Mn was excessively low. Accordingly, a strength of its steel material subjected to the induction hardening was low, and a Vickers hardness of its steel material subjected to the induction hardening was less than 730 HV. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test number 25, its content of Cr was excessively high. Accordingly, a strength of its steel material subjected to the induction hardening was low, and a Vickers hardness of its steel material subjected to the induction hardening was less than 730 HV. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. This is considered to be due to insufficient dissolution of cementite in the induction hardening, which failed to uniformly produce martensite through the hardening.
As to the test number 26, its content of Al was excessively high. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. This is considered to be due to formation of coarse Al2O3 inclusions in a large amount.
As to the test number 27, its content of Al was excessively low. As a result, its machinability was less than 135%, indicating that an excellent machinability was not obtained.
As to the test number 28, its content of B was excessively low. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. In addition, its bending fatigue strength was less than 115%, indicating that an excellent bending fatigue strength was not obtained.
As to the test number 29, the content of Ti was excessively low. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. In addition, its bending fatigue strength was less than 115%, indicating that an excellent bending fatigue strength was not obtained.
As to the test number 30, its content of Ca was excessively high. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. This is considered to be due to formation of coarse oxide inclusions.
As to the test number 31, its content of Ca was excessively low. Accordingly, its composite-inclusion ratio Ra was less than 20%. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test numbers 32 and 33, their Fn1s failed to satisfy Formula (1). Accordingly, bainite was produced in their micro-structures. As a result, its machinability was less than 135%, indicating that an excellent machinability was not obtained.
As to the test numbers 34 and 35, their Fn2s failed to satisfy Formula (2). Accordingly, their fractions of pearlite were less than 85%. As a result, imperfect hardening occurred, with the result that their Vickers hardnesses were less than 730 HV. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test numbers 36 and 37, their Fn3s failed to satisfy Formula (3). Accordingly, their Vickers hardnesses were less than 730 HV. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. This is considered to be due to undissolved cementite remaining during the induction hardening.
As to the test numbers 38 to 39, their chemical compositions were appropriate and satisfied Formulae (1) to (3). However, their ts/τ (retention time/mixing time) were low in the heating retaining step in the refining step. Accordingly, their composite-inclusion ratios Ra were less than 20%. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test number 40, its chemical composition was appropriate and satisfied Formulae (1) to (3). However, its order of adding Al, Si, and Ca was not appropriate. Accordingly, their composite-inclusion ratios Ra were less than 20%. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained.
As to the test number 41, its chemical composition was appropriate and satisfied Formulae (1) to (3). However, its average cooling rate after the finish rolling was excessively high. Accordingly, bainite was produced in their micro-structures. Accordingly, their fractions of pearlite were less than 85%. As a result, its surface fatigue strength was less than 100%, indicating that an excellent surface fatigue strength was not obtained. In addition, its bending fatigue strength was less than 115%, indicating that an excellent bending fatigue strength was not obtained. Furthermore, its machinability was less than 135%, indicating that an excellent machinability was not obtained.
The embodiment according to the present invention has been described above. However, the aforementioned embodiment is merely an example for practicing the present invention. Therefore, the present invention is not limited to the aforementioned embodiment, and the aforementioned embodiment can be modified and implemented as appropriate without departing from the scope of the present invention.
Claims
1. A steel for induction hardening comprising
- a chemical composition consisting of, in mass percent:
- C: 0.53 to less than 0.58%;
- Si: 0.70 to 1.40%;
- Mn: 0.20 to 1.40%;
- P: less than 0.020%;
- S: 0.025% or less;
- Al: more than 0.06% to 0.15%;
- N: 0.0020 to 0.0080%;
- O: 0.0015% or less;
- B: 0.0003 to 0.0040%;
- Ti: 0.010 to 0.050%;
- Ca: 0.0005 to 0.005%;
- Cr: 0 to 0.15%;
- Cu: 0 to 0.50%;
- Ni: 0 to 0.30%;
- Mo: 0 to 0.20%;
- V: 0 to 0.05%; and
- Nb: 0 to 0.05%,
- with the balance being Fe and impurities, and satisfying Formulae (1) to (3), wherein
- a steel microstructure is made up of ferrite and pearlite, where an area fraction of the pearlite is 85% or more, and
- in the steel, a ratio of a number of composite inclusions to a total number of Al2O3 inclusions and the composite inclusions is 20% or more, and the composite inclusions contain, in mass percent, 2.0% or more of SiO2 and 2.0% or more of CaO, with the 99% or more of the balance being Al2O3: C+Si/7+Mn/5+Cr/9+Mo/2.5≤0.98 (1) C+Si/10+Mn/20+Cr/25≥0.70 (2) Cr/Si≤0.20 (3)
- where, symbols of elements in Formulae (1) to (3) are to be substituted by contents of corresponding elements (mass percent).
2. The steel for induction hardening according to claim 1, wherein the chemical composition contains one or more types selected from the group consisting of:
- Cr: 0.05 to 0.15%;
- Cu: 0.03 to 0.50%;
- Ni: 0.03 to 0.30%; and
- Mo: 0.01 to 0.20%.
3. The steel for induction hardening according to claim 1, wherein the chemical composition contains one or more types selected from the group consisting of:
- V: 0.01 to 0.05%; and
- Nb: 0.01 to 0.05%.
4. The steel for induction hardening according to claim 2, wherein the chemical composition contains one or more types selected from the group consisting of:
- V: 0.01 to 0.05%; and
- Nb: 0.01 to 0.05%.
Type: Application
Filed: Jul 19, 2017
Publication Date: Oct 3, 2019
Inventors: Kei Miyanishi (Chiyoda-ku, Tokyo), Yutaka Neishi (Chiyoda-ku, Tokyo), Akira Shiga (Chiyoda-ku, Tokyo)
Application Number: 16/317,086
