JP6459955B2 - rail - Google Patents

Description

  The present invention relates to a high ductility rail.

  In high-axle heavy railways that mainly transport ores, the load applied to the axles of freight cars is much higher than that of passenger cars, and the use environment of rails and wheels is also severe. Conventionally, steel having a pearlite structure has been mainly used in such high-axle railways, that is, rails used in railways with heavy loading weights of trains and freight cars, from the viewpoint of wear resistance. However, in recent years, it has been required to further improve the wear resistance and fatigue damage resistance of the rail in order to increase the loading weight on the freight car and improve the transportation efficiency. Further, in addition to an increase in load weight, a deterioration of the rail laying environment such as damage to sleepers and ground depression causes an increase in the force (tensile stress) applied to the rail, and as a result, rail breakage becomes a problem.

  Therefore, various methods have been proposed to solve these problems. For example, Patent Documents 1 and 2 propose pearlite rails that have a specified number of pearlite blocks and are excellent in wear resistance and ductility.

Japanese Patent No. 4272385 JP 2002-212777 A

  However, in order to improve ductility, it is necessary to suppress the accumulation of dislocations during tension and the generation of voids due to the accumulation of dislocations. In Patent Documents 1 and 2, it is said that the ductility of the rail is improved by controlling the number of pearlite blocks in the pearlite rail. However, in the pearlite rail, dislocations accumulate on the boundary of the pearlite block and voids are generated. The fact is that ductility cannot be improved sufficiently only by reducing the block size.

  This invention is made | formed in view of the said actual condition, It aims at providing the high ductility pearlite type rail which is excellent in ductility and can be used conveniently also in a high axle load railway. Here, “pearlite type” means that the steel having a pearlite structure has a structure different from the pearlite structure, which can be obtained by subjecting steel having a pearlite structure to heat treatment under specific conditions as described later.

  As a result of studies to solve the above problems, the present inventors have found that the ductility can be improved more than that of conventional pearlite rails by optimizing the component composition and lamellar fraction of the rails.

This invention is made | formed based on the said knowledge, The summary structure is as follows.
1. % By weight
C: 0.70 to 0.85%,
Si: 0.10 to 1.50%,
Mn: 0.40 to 1.50%,
P: 0.035% or less,
S: 0.0005 to 0.010% or less, and Cr: 0.05 to 1.50%,
The balance has a component composition consisting essentially of Fe and inevitable impurities,
The rail whose lamellar fraction defined by the following formula (1) is 40 to 98%.
Lamella fraction = {1− (area of cementite having an aspect ratio of 5 or less / total area of cementite)} × 100 (1)

2. The component composition is mass%,
V: 0.30% or less,
Cu: 1.0% or less,
Ni: 1.0% or less,
Nb: 0.05% or less,
Mo: 0.5% or less,
Al: 0.07% or less,
W: 1.0% or less,
The rail according to 1 above, further containing one or more selected from the group consisting of B: 0.005% or less, and Ti: 0.05% or less.

  ADVANTAGE OF THE INVENTION According to this invention, it is excellent in ductility and can provide the highly ductile pearlite type rail which can be used suitably also in a high axle load railway.

It is a schematic diagram of the rail head which shows the collection position of a tensile test piece. It is a scanning electron micrograph of the microstructure when the lamellar fraction is 100%, 85%, and 30%.

[Ingredient composition]
A method for carrying out the present invention will be specifically described. In the present invention, it is important that the rail has the above component composition. First, the reason why the component composition is limited as described above in the present invention will be described. The unit of the content of each component is “mass%” but is abbreviated as “%”.

C: 0.70 to 0.85%
C is an element that has the effect of forming cementite in the pearlite structure and improving the strength. Therefore, the addition of C is indispensable to ensure the strength of the rail, and the strength is improved as the C content is increased. When the lamellar fraction is 98% or less as in the present invention, the strength tends to be lower than that of a conventional pearlite rail, so that an excellent strength can be obtained when the C content is less than 0.70%. difficult. On the other hand, if the C content exceeds 0.85%, proeutectoid cementite is generated at the austenite grain boundaries during transformation after hot rolling, so that the ductility of the rail is lowered. Therefore, the C content is 0.70 to 0.85%.

Si: 0.10 to 1.50%
Si is an element having an effect as a deoxidizer. Si has an effect of improving the strength of the rail by solid solution strengthening to ferrite in the pearlite structure. In order to acquire the said effect, it is necessary to make Si content 0.10% or more. On the other hand, when the Si content exceeds 1.50%, a large amount of oxide inclusions are generated due to the bonding force with high oxygen that Si has. Moreover, since strength increases by solid solution strengthening, ductility falls. Therefore, the Si content is set to 0.10 to 1.50%.

Mn: 0.40 to 1.50%
Mn is an element that contributes to increasing the strength and ductility of the rail by lowering the transformation temperature and reducing the lamellar spacing. However, if the Mn content is less than 0.40%, a sufficient effect cannot be obtained. On the other hand, if the Mn content exceeds 1.50%, a martensitic structure due to microsegregation of the steel tends to occur, and as a result, the ductility decreases. Therefore, the Mn content is 0.40 to 1.50%.

P: 0.035% or less When the P content exceeds 0.035%, the ductility of the rail decreases. Therefore, the P content is 0.035% or less. On the other hand, the lower limit of the P content is not particularly limited, and may be 0%, but industrially exceeds 0%. Furthermore, if the P content is excessively reduced, refining costs are increased, so the P content is preferably 0.020% or more.

S: 0.0005 to 0.010%
S is present in steel mainly in the form of A-based (sulfide-based) inclusions. When the S content exceeds 0.010%, the amount of the inclusions is remarkably increased and coarse inclusions are generated, so that ductility is lowered. On the other hand, when the S content is less than 0.0005%, the cost of the rail steel increases. Therefore, the S content is set to 0.0005 to 0.010%.

Cr: 0.05-1.50%
Cr is an element having an effect of improving strength by solid solution strengthening to cementite in a pearlite structure. In order to acquire the said effect, it is necessary to make Cr content 0.05% or more. On the other hand, if the Cr content exceeds 1.50%, the strength increases due to the solid solution strengthening of Cr, and as a result, ductility decreases. Therefore, the Cr content is 0.05 to 1.50%.

  The rail in one embodiment of the present invention has a component composition composed of the above components, the remaining Fe and inevitable impurities. Note that rails containing other trace elements also belong to the present invention within a range that does not substantially affect the operational effects of the present invention.

In addition, the above component composition is mass%,
V: 0.30% or less,
Cu: 1.0% or less,
Ni: 1.0% or less,
Nb: 0.05% or less,
Mo: 0.5% or less,
Al: 0.07% or less,
W: 1.0% or less,
One type or two or more types selected from the group consisting of B: 0.005% or less and Ti: 0.05% or less can be further contained as necessary.

V: 0.30% or less V is an element that precipitates as carbonitride during and after rolling and has the effect of improving strength and ductility by precipitation strengthening. However, if the V content exceeds 0.30%, a large amount of coarse carbonitride precipitates, resulting in a decrease in ductility. Therefore, when adding V, it is preferable to make V content 0.30% or less. On the other hand, the lower limit of the V content is not particularly limited, but is preferably 0.001% or more in order to exhibit the above effects.

Cu: 1.0% or less Cu, like Cr, is an element having an effect of improving strength by solid solution strengthening. However, if the Cu content exceeds 1.0%, Cu cracking occurs. Therefore, when adding Cu, it is preferable to make Cu content 1.0% or less. On the other hand, the lower limit of the Cu content is not particularly limited, but is preferably 0.001% or more in order to exhibit the above effects.

Ni: 1.0% or less Ni is an element having an effect of improving strength without deteriorating ductility. Moreover, since Cu cracking can be suppressed by adding Ni in combination with Cu, it is desirable to add Ni when Cu is added. However, if the Ni content exceeds 1.0%, the hardenability increases and martensite is generated, resulting in a decrease in ductility. Therefore, when adding Ni, it is preferable to make Ni content into 1.0% or less. On the other hand, the lower limit of the Ni content is not particularly limited, but is preferably 0.001% or more in order to exhibit the above effects.

Nb: 0.05% or less Nb precipitates as carbonitride during and after rolling, and improves the strength and ductility of pearlite. However, when the Nb content exceeds 0.05%, a large amount of coarse carbonitride precipitates, so that ductility decreases. Therefore, when adding Nb, it is preferable to make Nb content 0.05% or less. On the other hand, the lower limit of the Nb content is not particularly limited, but is preferably 0.001% or more in order to develop the effect of improving the strength and ductility.

Mo: 0.5% or less Mo precipitates as carbide during and after rolling, and improves strength and ductility by precipitation strengthening. However, when the Mo content exceeds 0.5%, martensite is generated, and as a result, ductility is lowered. Therefore, when adding Mo, it is preferable to make Mo content into 0.5% or less. On the other hand, the lower limit of the Mo content is not particularly limited, but is preferably 0.001% or more in order to exhibit the above-described effects of improving the strength and ductility.

Al: 0.07% or less Al is an element added as a deoxidizer. However, if the Al content exceeds 0.07%, a large amount of oxide inclusions are generated due to the high bonding strength with Al, and as a result, the ductility decreases. Therefore, the Al content is preferably 0.07% or less. On the other hand, the lower limit of the Al content is not particularly limited, but is preferably 0.001% or more for deoxidation.

W: 1.0% or less W precipitates as a carbide during and after rolling, and improves strength and ductility by precipitation strengthening. However, when the W content exceeds 1.0%, martensite is generated, and as a result, ductility is lowered. Therefore, when adding W, it is preferable to make W content into 1.0% or less. On the other hand, the lower limit of the W content is not particularly limited, but is preferably 0.001% or more in order to develop the effect of improving the strength and ductility.

B: 0.005% or less B precipitates as a nitride during and after rolling, and improves strength and ductility by precipitation strengthening. However, when the B content exceeds 0.005%, martensite is generated, and as a result, ductility is lowered. Therefore, when adding B, it is preferable to make B content 0.005% or less. On the other hand, the lower limit of the B content is not particularly limited, but is preferably 0.0001% or more in order to develop the effect of improving the strength and ductility.

Ti: 0.05% or less Ti precipitates as carbide, nitride or carbonitride during and after rolling, and improves strength and ductility by precipitation strengthening. However, if the Ti content exceeds 0.05%, coarse carbides, nitrides or carbonitrides are produced, and as a result, ductility is lowered. Therefore, when adding Ti, it is preferable to make Ti content 0.05% or less. On the other hand, the lower limit of the Ti content is not particularly limited, but is preferably 0.001% or more in order to exhibit the above-described effects of improving the strength and ductility.

[Lamellar fraction]
Lamella fraction is 40-98%
In the present invention, it is important that the rail has a structure in which the lamellar fraction defined by the following formula (1) is 40 to 98% in addition to the above component composition.
Lamella fraction = {1− (area of cementite having an aspect ratio of 5 or less / total area of cementite)} × 100 (1)

  In order to improve the ductility of the rail, it is necessary to suppress the generation of voids when the rails are subjected to tensile stress and the connection of the generated voids. Voids are created at pearlite block boundaries, which connect and lead to breakage. Therefore, in order to suppress the generation of voids, it is effective to reduce the pearlite block boundary, and the pearlite block boundary can be reduced by reducing a region having a lamellar structure.

  When the lamellar fraction is greater than 98%, the reduction of the pearlite block boundary is insufficient, and the ductility is poor. On the other hand, when the lamellar fraction is less than 40%, the generation and connection of voids can be suppressed, but the tensile strength is lowered, so there is a concern that the wear resistance of the rail is lowered. Therefore, the lamellar fraction is 40 to 98%. Here, the values of “area of cementite having an aspect ratio of 5 or less” and “total area of cementite” can be measured by the methods described in the examples. Note that scanning electron micrographs of the microstructure when the lamellar fraction is 100%, 85%, and 30% are shown in FIG.

[Production method]
Next, a method for manufacturing the rail of the present invention will be described. Although the manufacturing method of the rail in this invention is not specifically limited, After manufacturing a rail by hot rolling, it can manufacture by performing the process hold | maintained at specific temperature.

  The manufacture of rails by hot rolling can be performed, for example, by the following procedure. First, steel is melted in a converter or an electric furnace, and the composition of the steel is adjusted to the above range through secondary refining such as degassing as necessary. Subsequently, continuous casting is performed to obtain a bloom, and the obtained bloom is gradually cooled at a cooling rate of 0.5 ° C./s or less for 40 to 150 hours. Next, after heating the said bloom at 1200-1350 degreeC with a heating furnace, it hot-rolls and makes it a rail. The hot rolling is preferably performed at a rolling end temperature of 850 to 1000 ° C., and the rail after hot rolling is preferably cooled at a cooling rate of 1 to 5 ° C./s.

  If the heating temperature at the time of the heating is less than 1200 ° C., the rolling load during hot rolling becomes too large, and it becomes difficult to roll the rail to a desired shape. On the other hand, when the heating temperature exceeds 1350 ° C., melting occurs in a part of the steel, and cracks are likely to occur during hot rolling on the rail. Moreover, when the rolling end temperature at the time of hot rolling is less than 850 ° C., the rolling load at the time of hot rolling becomes too large, and it becomes difficult to roll the rail to a desired shape. On the other hand, when the rolling end temperature exceeds 1000 ° C., martensite is likely to occur in the steel structure even if the above cooling rate is adopted during subsequent cooling. When the cooling rate after hot rolling is less than 1 ° C./s, the lamellar spacing in the steel structure increases, and the strength of the rail decreases. On the other hand, when the cooling rate after hot rolling exceeds 5 ° C./s, martensite is likely to occur in the steel structure.

  At this time, in order to control the lamellar fraction to 40 to 98%, either (1) after cooling following the hot rolling is completed, or (2) during the cooling following the hot rolling, At the timing, a process of holding the rail at a specific temperature is performed.

  (1) When the holding is performed after the cooling following the hot rolling is completed, the rail after the cooling is held in a temperature range of 300 to 650 ° C. for 900 to 360,000 seconds using a furnace or a high-frequency heat treatment apparatus. (Tempering)

(2) When the holding is performed during the cooling following the hot rolling, the cooling is stopped when the rail temperature becomes 300 to 650 ° C during the cooling, and the temperature range is 300 to 650 ° C. In addition, a process of holding for 900 to 360,000 seconds is performed.

Example 1
Rails were prepared by hot rolling steel having the composition shown in Table 1. At that time, the heating temperature before hot rolling was 1250 ° C., the rolling exit temperature was 900 ° C., and the rail after hot rolling was cooled at 2 ° C./s. Thereafter, the rail after completion of cooling was tempered under the conditions shown in Table 2. In addition, No. In the comparative examples 1 and 2, tempering was not performed. Each of the obtained rails was subjected to a tensile test to measure 0.2% proof stress, tensile strength, and elongation. Moreover, the microstructure was observed and the lamellar fraction of each rail was calculated | required. The measurement method was as follows.

[Tensile test]
Tensile test pieces were collected from the heads of the obtained rails. As the tensile test piece, 2.13.4. Of AREMA Chapter 4. From the position described in 1., a tensile test piece having a parallel portion of 12.7 mm described in ASTM A370 was collected. Next, using the obtained tensile test piece, a tensile test was performed under the conditions of a tensile speed of 1 mm / min and a distance between ratings: 50 mm, and 0.2% proof stress, tensile strength, and elongation were measured. The measured values are as shown in Table 2.

[Lamellar fraction]
From the same position from which the tensile test piece was collected, a microscopic observation specimen having a diameter of 12.5 mm × 5 mm was collected. The obtained specimen for microstructural observation was embedded in a resin, and the cross section was mirror-polished and then corroded with 1% nital. Thereafter, using a scanning electron microscope (SEM), observation and photographing of the cross section were performed at a magnification of 15000 and 20 fields of view, and the cementite area in the photographed image was traced and analyzed. The aspect ratio was determined. Table 2 shows the lamellar fraction obtained from the measured value based on the above equation (1).

  Comparative Example No. in the above example. Rail No. 1 is a currently used pearlite rail having a C content of 0.81%. As can be seen from the results shown in Table 2, all of the rails of the inventive examples that satisfy the conditions of the present invention have the comparative example No. It exhibited an elongation (elongation: 14.4% or more) that was 20% or better than that of No. 1 rail, and had a tensile strength of 950 MPa or more. On the other hand, the rail of the comparative example that does not satisfy the conditions of the present invention was inferior in at least one of tensile strength and elongation.

(Example 2)
A rail was prepared in the same manner as in Example 1 except that steel having the component composition shown in Table 3 was used, and a tensile test and a lamellar fraction were measured in the same manner as in Example 1. Table 4 shows the tempering conditions and the measurement results. In addition, No. In 13 comparative examples, tempering was not performed.

  As can be seen from the results shown in Table 4, all of the rails of the inventive examples satisfying the conditions of the present invention had excellent elongation and tensile strength. On the other hand, the rail of the comparative example that does not satisfy the conditions of the present invention was inferior in at least one of tensile strength and elongation.

Claims (2)

% By weight
C: 0.70 to 0.85%,
Si: 0.10 to 1.50%,
Mn: 0.40 to 1.50%,
P: 0.035% or less,
S: 0.0005-0.010%, and Cr: 0.05-1.50%,
The balance has a component composition consisting of Fe and inevitable impurities,
(1) below the lamellar fraction defined by equation Ri 40-98% der,
A pearlitic rail having an elongation of 14.4% or more and a tensile strength of 950 MPa or more .
Lamella fraction = {1− (area of cementite having an aspect ratio of 5 or less / total area of cementite)} × 100 (1) The component composition is mass%,
V: 0.30% or less,
Cu: 1.0% or less,
Ni: 1.0% or less,
Nb: 0.05% or less,
Mo: 0.5% or less,
Al: 0.07% or less,
W: 1.0% or less,
The rail according to claim 1, further comprising one or more selected from the group consisting of B: 0.005% or less, and Ti: 0.05% or less.