CA3157401C - Rail and method for producing the same - Google Patents
Rail and method for producing the same Download PDFInfo
- Publication number
- CA3157401C CA3157401C CA3157401A CA3157401A CA3157401C CA 3157401 C CA3157401 C CA 3157401C CA 3157401 A CA3157401 A CA 3157401A CA 3157401 A CA3157401 A CA 3157401A CA 3157401 C CA3157401 C CA 3157401C
- Authority
- CA
- Canada
- Prior art keywords
- mass
- web
- less
- rail
- pearlite
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 31
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 59
- 239000000203 mixture Substances 0.000 claims abstract description 22
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 46
- 238000001816 cooling Methods 0.000 claims description 33
- 239000000126 substance Substances 0.000 claims description 15
- 230000009467 reduction Effects 0.000 claims description 13
- 230000009466 transformation Effects 0.000 claims description 13
- 238000000034 method Methods 0.000 claims description 7
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 244000126002 Ziziphus vulgaris Species 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 description 21
- 239000010959 steel Substances 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 16
- 230000000694 effects Effects 0.000 description 16
- 229910000734 martensite Inorganic materials 0.000 description 15
- 239000010955 niobium Substances 0.000 description 13
- 239000010949 copper Substances 0.000 description 12
- 239000011572 manganese Substances 0.000 description 12
- 238000012360 testing method Methods 0.000 description 12
- 239000011651 chromium Substances 0.000 description 11
- 229910001566 austenite Inorganic materials 0.000 description 10
- 229910001567 cementite Inorganic materials 0.000 description 10
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 238000001953 recrystallisation Methods 0.000 description 8
- 229910001563 bainite Inorganic materials 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 206010053759 Growth retardation Diseases 0.000 description 4
- 231100000001 growth retardation Toxicity 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 230000005855 radiation Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 230000004888 barrier function Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 230000003111 delayed effect Effects 0.000 description 2
- 238000001887 electron backscatter diffraction Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/08—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling structural sections, i.e. work of special cross-section, e.g. angle steel
- B21B1/085—Rail sections
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B5/00—Rails; Guard rails; Distance-keeping means for them
- E01B5/02—Rails
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Structural Engineering (AREA)
- Civil Engineering (AREA)
- Architecture (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
A rail 1 comprises a foot section 2, a web section 3, and a head section 4. The component composition of the web section 3 includes C: 0.70-1.20 wt%, Si: 0.20-1.20 wt%, Mn: 0.20-1.50 wt%, P: 0.035 wt% or less, and Cr: 0.20-2.50 wt%, with the remainder comprising Fe and unavoidable impurities. The area ratio of pearlite in the web section 3 is 95% or more, and the average size of the pearlite blocks is 60 µm or less.
Description
DESCRIPTION
Title of Invention: RAIL AND METHOD FOR PRODUCING THE SAME
Technical Field [0001]
The present invention relates to a railroad rail having a foot, a web, and a head and to a method for producing the rail.
Background Art
Title of Invention: RAIL AND METHOD FOR PRODUCING THE SAME
Technical Field [0001]
The present invention relates to a railroad rail having a foot, a web, and a head and to a method for producing the rail.
Background Art
[0002]
In heavy haul railroads mainly used to transport ore and other materials, the load on the axles of freight cars is much higher than that on the axles of passenger cars, and rails are used in harsh environments. The efficiency of transportation in railroads has been improved by further increasing the carrying capacity of freight cars. There is thus a need for improvements in wear resistance, fatigue damage resistance, and delayed fracture resistance.
In heavy haul railroads mainly used to transport ore and other materials, the load on the axles of freight cars is much higher than that on the axles of passenger cars, and rails are used in harsh environments. The efficiency of transportation in railroads has been improved by further increasing the carrying capacity of freight cars. There is thus a need for improvements in wear resistance, fatigue damage resistance, and delayed fracture resistance.
[0003]
There have been various proposes for improving the wear resistance and other properties of rails, such as controlling the materials of rails, or using a special heat treatment in the production method (e.g., see Patent Literature 1 to Patent Literature 8). Patent Literature 1 and Patent Literature 2 each disclose a rail with its wear resistance improved by increasing the C content to more than Date Recue/Date Received 2022-04-06 0.85 mass% and 1.20 mass% or less. Patent Literature 3 and Patent Literature 4 each disclose a rail with its wear resistance improved by setting the C content to more than 0.85 mass% and 1.20 mass% or less and increasing the cementite fraction by heating the head of the rail.
There have been various proposes for improving the wear resistance and other properties of rails, such as controlling the materials of rails, or using a special heat treatment in the production method (e.g., see Patent Literature 1 to Patent Literature 8). Patent Literature 1 and Patent Literature 2 each disclose a rail with its wear resistance improved by increasing the C content to more than Date Recue/Date Received 2022-04-06 0.85 mass% and 1.20 mass% or less. Patent Literature 3 and Patent Literature 4 each disclose a rail with its wear resistance improved by setting the C content to more than 0.85 mass% and 1.20 mass% or less and increasing the cementite fraction by heating the head of the rail.
[0004]
Patent Literature 5 proposes a rail with its fatigue damage resistance improved by suppressing formation of pro-eutectoid cementite by addition of Al and Si. Patent Literature 6 discloses a rail with its service life improved by setting, to Hv 370 or higher, the Vickers hardness in a region from the surface of the corners and top of the head of the rail to a depth of at least 20 mm.
Patent Literature 5 proposes a rail with its fatigue damage resistance improved by suppressing formation of pro-eutectoid cementite by addition of Al and Si. Patent Literature 6 discloses a rail with its service life improved by setting, to Hv 370 or higher, the Vickers hardness in a region from the surface of the corners and top of the head of the rail to a depth of at least 20 mm.
[0005]
Patent Literature 7 discloses a method for forming a tempered martensite microstructure having high toughness in a web. The method includes rapidly cooling the web at a cooling rate of 15 C/sec or higher, then stopping cooling at a temperature of 250 to 450 C, and when the bainite transformation reaches 30% or more, cooling the web to the Ms temperature or lower, forming a martensite microstructure. Patent Literature 8 discloses that the crack growth resistance of the web is provided by imparting compressive residual stress by cooling a rail from the top of the head to the upper neck or to the web with high Date Recue/Date Received 2022-04-06 pressure gas or water-containing gas.
Citation List Patent Literature
Patent Literature 7 discloses a method for forming a tempered martensite microstructure having high toughness in a web. The method includes rapidly cooling the web at a cooling rate of 15 C/sec or higher, then stopping cooling at a temperature of 250 to 450 C, and when the bainite transformation reaches 30% or more, cooling the web to the Ms temperature or lower, forming a martensite microstructure. Patent Literature 8 discloses that the crack growth resistance of the web is provided by imparting compressive residual stress by cooling a rail from the top of the head to the upper neck or to the web with high Date Recue/Date Received 2022-04-06 pressure gas or water-containing gas.
Citation List Patent Literature
[0006]
PTL 1: Japanese Unexamined Patent Application Publication No. 8-109439 PTL 2: Japanese Unexamined Patent Application Publication No. 8-144016 PTL 3: Japanese Unexamined Patent Application Publication No. 8-246100 PTL 4: Japanese Unexamined Patent Application Publication No. 8-246101 PTL 5: Japanese Unexamined Patent Application Publication No. 2002-69585 PTL 6: Japanese Unexamined Patent Application Publication No. 10-195601 PTL 7: Japanese Unexamined Patent Application Publication No. 62-99438 PTL 8: Japanese Unexamined Patent Application Publication No. 59-47326 Summary of Invention Technical Problem
PTL 1: Japanese Unexamined Patent Application Publication No. 8-109439 PTL 2: Japanese Unexamined Patent Application Publication No. 8-144016 PTL 3: Japanese Unexamined Patent Application Publication No. 8-246100 PTL 4: Japanese Unexamined Patent Application Publication No. 8-246101 PTL 5: Japanese Unexamined Patent Application Publication No. 2002-69585 PTL 6: Japanese Unexamined Patent Application Publication No. 10-195601 PTL 7: Japanese Unexamined Patent Application Publication No. 62-99438 PTL 8: Japanese Unexamined Patent Application Publication No. 59-47326 Summary of Invention Technical Problem
[0007]
According to the rails in Patent Literature 1 to Patent Literature 6, the head of each rail which mainly come into Date Recue/Date Received 2022-04-06 contact with wheel flanges has high wear resistance.
However, the materials of the web of the rail are not sufficiently controlled, and the web may undergo crack growth depending on production method.
According to the rails in Patent Literature 1 to Patent Literature 6, the head of each rail which mainly come into Date Recue/Date Received 2022-04-06 contact with wheel flanges has high wear resistance.
However, the materials of the web of the rail are not sufficiently controlled, and the web may undergo crack growth depending on production method.
[0008]
The technique of Patent Literature 7 requires maintaining the temperature until bainite transformation starts, which reduces production efficiency. The technique disclosed in Patent Literature 8 puts the most importance on the wear resistance/fatigue damage resistance of the head and may not provide the web with desired crack growth resistance, and the martensite microstructure highly susceptible to cracking may be formed depending on production conditions.
The technique of Patent Literature 7 requires maintaining the temperature until bainite transformation starts, which reduces production efficiency. The technique disclosed in Patent Literature 8 puts the most importance on the wear resistance/fatigue damage resistance of the head and may not provide the web with desired crack growth resistance, and the martensite microstructure highly susceptible to cracking may be formed depending on production conditions.
[0009]
The present invention has been made in light of the above circumstances. An object of the present invention is to provide a rail and a method for producing the rail in which rail breakage is prevented by suppressing web crack growth while the production efficiency is improved.
Solution to Problem
The present invention has been made in light of the above circumstances. An object of the present invention is to provide a rail and a method for producing the rail in which rail breakage is prevented by suppressing web crack growth while the production efficiency is improved.
Solution to Problem
[0010]
The present invention has been made to achieve the above object. The gist of the present invention is as described below.
Date Recue/Date Received 2022-04-06 [1] A rail includes a foot, a web, and a head, wherein the web has a chemical composition containing:
C: 0.70 to 1.20 mass%, Si: 0.20 to 1.20 mass%, Mn: 0.20 to 1.50 mass%, P: 0.035 mass% or less, S: 0.0005 to 0.012 mass%, and Cr: 0.20 to 2.50 mass%, with the balance being Fe and incidental impurities, an area fraction of pearlite in the web is 95% or more, and an average size of pearlite blocks is 60 m or less. In some embodiments, the average size of pearlite blocks is 30 m or less.
[2] In the rail according to [1], the chemical composition further contains one or two or more selected from Cu: 1.0 mass%
or less, Ni: 1.0 mass% or less, Nb: 0.05 mass% or less, Mo:
1.0 mass% or less, V: 0.005 to 0.10 mass%, W: 1.0 mass% or less and B: 0.005 mass% or less.
[3] In the rail according to [1] or [2], a crack growth rate da/dN (m/cycle) in the web at a stress intensity factor AK - 20 MPa=m1/2 is 8.0 x 10-8 or less.
[4] A rail production method for producing a rail from a slab having the chemical composition according to any one of [1] to [3] includes:
performing finish rolling at a finishing temperature of 1000 C or lower in such a manner that a reduction in area of a web is 10% or more; and after finish rolling, cooling the web at a cooling rate of 1 Date Recue/Date Received 2023-06-01 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C
to 600 C.
[4a] A rail production method for producing the rail according to any one of [1] to [3] from a slab having the chemical composition, the method including:
performing finish rolling at a finishing temperature of 1000 C or lower in such a manner that a reduction in area of a web is 10% or more; and after finish rolling, cooling the web at a cooling rate of 1 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C
to 600 C.
[5] In the rail production method according to [4] or [4a], wherein the finishing temperature in finish-rolling the web is in a range of 800 C to 900 C.
Advantageous Effects of Invention
The present invention has been made to achieve the above object. The gist of the present invention is as described below.
Date Recue/Date Received 2022-04-06 [1] A rail includes a foot, a web, and a head, wherein the web has a chemical composition containing:
C: 0.70 to 1.20 mass%, Si: 0.20 to 1.20 mass%, Mn: 0.20 to 1.50 mass%, P: 0.035 mass% or less, S: 0.0005 to 0.012 mass%, and Cr: 0.20 to 2.50 mass%, with the balance being Fe and incidental impurities, an area fraction of pearlite in the web is 95% or more, and an average size of pearlite blocks is 60 m or less. In some embodiments, the average size of pearlite blocks is 30 m or less.
[2] In the rail according to [1], the chemical composition further contains one or two or more selected from Cu: 1.0 mass%
or less, Ni: 1.0 mass% or less, Nb: 0.05 mass% or less, Mo:
1.0 mass% or less, V: 0.005 to 0.10 mass%, W: 1.0 mass% or less and B: 0.005 mass% or less.
[3] In the rail according to [1] or [2], a crack growth rate da/dN (m/cycle) in the web at a stress intensity factor AK - 20 MPa=m1/2 is 8.0 x 10-8 or less.
[4] A rail production method for producing a rail from a slab having the chemical composition according to any one of [1] to [3] includes:
performing finish rolling at a finishing temperature of 1000 C or lower in such a manner that a reduction in area of a web is 10% or more; and after finish rolling, cooling the web at a cooling rate of 1 Date Recue/Date Received 2023-06-01 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C
to 600 C.
[4a] A rail production method for producing the rail according to any one of [1] to [3] from a slab having the chemical composition, the method including:
performing finish rolling at a finishing temperature of 1000 C or lower in such a manner that a reduction in area of a web is 10% or more; and after finish rolling, cooling the web at a cooling rate of 1 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C
to 600 C.
[5] In the rail production method according to [4] or [4a], wherein the finishing temperature in finish-rolling the web is in a range of 800 C to 900 C.
Advantageous Effects of Invention
[0011]
According to the present invention, it is possible to reduce the crack growth rate in the web and thus to suppress the crack growth in the web and the breakage of the rail.
Brief Description of Drawings
According to the present invention, it is possible to reduce the crack growth rate in the web and thus to suppress the crack growth in the web and the breakage of the rail.
Brief Description of Drawings
[0012]
[Fig. 1] Fig. 1 is a perspective view of a rail according to a preferred embodiment of the present invention.
[Fig. 2] Fig. 2 is a plan view of the rail according to the preferred embodiment of the present invention.
Date Recue/Date Received 2023-06-01 ¨ 6a ¨
[Fig. 31! Fig. 3 is a schematic view of an example rail production system used in a rail production method according to the present invention.
[Fig. 4] Fig. 4 is a schematic view of an example test specimen used in a web crack growth test.
Date Recue/Date Received 2023-06-01 Description of Embodiments
[Fig. 1] Fig. 1 is a perspective view of a rail according to a preferred embodiment of the present invention.
[Fig. 2] Fig. 2 is a plan view of the rail according to the preferred embodiment of the present invention.
Date Recue/Date Received 2023-06-01 ¨ 6a ¨
[Fig. 31! Fig. 3 is a schematic view of an example rail production system used in a rail production method according to the present invention.
[Fig. 4] Fig. 4 is a schematic view of an example test specimen used in a web crack growth test.
Date Recue/Date Received 2023-06-01 Description of Embodiments
[0013]
Embodiments of the present invention will be described below. Fig. 1 is a schematic view of a rail according to a preferred embodiment of the present invention. A rail 1 in Fig. 1 supports the load for passenger railroads or freight railroads and guides railroad cars in the running direction (direction of arrow Y). The rail 1 has a foot (bottom) 2, a web 3, and a head 4.
Embodiments of the present invention will be described below. Fig. 1 is a schematic view of a rail according to a preferred embodiment of the present invention. A rail 1 in Fig. 1 supports the load for passenger railroads or freight railroads and guides railroad cars in the running direction (direction of arrow Y). The rail 1 has a foot (bottom) 2, a web 3, and a head 4.
[0014]
The foot 2 will be placed on railroad ties and has a cross section widening in the width direction (direction of arrow X). The web 3 has a shape extending vertically (direction of arrow Z) from the foot 2 and has a function of ensuring bending stiffness as a beam of the rail 1 itself.
The head 4, which is located on the web 3, comes into contact with the wheels of trains and directly supports the load of the trains. As a train runs on the rail 1, the load from the wheels of the train is transmitted from the head 4 to the web 3 and from the web 3 to the foot 2.
The foot 2 will be placed on railroad ties and has a cross section widening in the width direction (direction of arrow X). The web 3 has a shape extending vertically (direction of arrow Z) from the foot 2 and has a function of ensuring bending stiffness as a beam of the rail 1 itself.
The head 4, which is located on the web 3, comes into contact with the wheels of trains and directly supports the load of the trains. As a train runs on the rail 1, the load from the wheels of the train is transmitted from the head 4 to the web 3 and from the web 3 to the foot 2.
[0015]
Since the web 3 does not directly come into contact with the wheels unlike the head 4, the web 3 does not need to have wear resistance equivalent to that of the head 4.
The web 3 transmits the wheel weight on the head 4 to the Date Recue/Date Received 2022-04-06 foot 2. When the wheel weight is applied eccentrically from the center of the head 4 in the width direction, the web 3 may undergo bending stress to cause horizontal cracks. For this, the web 3 needs to have high crack growth resistance.
The web 3 of the rail 1 thus has the following chemical composition and steel microstructure.
Since the web 3 does not directly come into contact with the wheels unlike the head 4, the web 3 does not need to have wear resistance equivalent to that of the head 4.
The web 3 transmits the wheel weight on the head 4 to the Date Recue/Date Received 2022-04-06 foot 2. When the wheel weight is applied eccentrically from the center of the head 4 in the width direction, the web 3 may undergo bending stress to cause horizontal cracks. For this, the web 3 needs to have high crack growth resistance.
The web 3 of the rail 1 thus has the following chemical composition and steel microstructure.
[0016]
The rail 1 contains C: 0.70 to 1.20 mass%, Si: 0.20 to 1.20 mass%, Mn: 0.20 to 1.50 mass%, P: 0.035 mass% or less, S: 0.0005 to 0.012 mass%, and Cr: 0.20 to 2.50 mass%. The composition components will be described below separately.
The rail 1 contains C: 0.70 to 1.20 mass%, Si: 0.20 to 1.20 mass%, Mn: 0.20 to 1.50 mass%, P: 0.035 mass% or less, S: 0.0005 to 0.012 mass%, and Cr: 0.20 to 2.50 mass%. The composition components will be described below separately.
[0017]
C: 0.70 to 1.20 mass%
Carbon C is an essential element for ensuring the strength, or fatigue damage resistance, of a pearlite microstructure. The fatigue damage resistance increases as the C content increases. With a C content of less than 0.70 mass%, it is difficult to provide higher fatigue damage resistance than that of a conventional heat-treated type pearlite steel rail. With a C content of more than 1.20 mass%, considerable amount of pro-eutectoid cementite is formed at austenite grain boundaries during pearlite transformation after hot rolling, and the fatigue damage resistance remarkably decreases. Pro-eutectoid cementite is also found when the C content is 1.20 mass% or less, but it Date Recue/Date Received 2022-04-06 is formed in trace amounts. Pro-eutectoid cementite thus has a miner effect on the fatigue damage resistance.
Therefore, the C content is 0.70 to 1.20 mass%. The C
content is preferably 0.75 to 1.00 mass%. The C content is more preferably 0.75 to 0.85 mass%.
C: 0.70 to 1.20 mass%
Carbon C is an essential element for ensuring the strength, or fatigue damage resistance, of a pearlite microstructure. The fatigue damage resistance increases as the C content increases. With a C content of less than 0.70 mass%, it is difficult to provide higher fatigue damage resistance than that of a conventional heat-treated type pearlite steel rail. With a C content of more than 1.20 mass%, considerable amount of pro-eutectoid cementite is formed at austenite grain boundaries during pearlite transformation after hot rolling, and the fatigue damage resistance remarkably decreases. Pro-eutectoid cementite is also found when the C content is 1.20 mass% or less, but it Date Recue/Date Received 2022-04-06 is formed in trace amounts. Pro-eutectoid cementite thus has a miner effect on the fatigue damage resistance.
Therefore, the C content is 0.70 to 1.20 mass%. The C
content is preferably 0.75 to 1.00 mass%. The C content is more preferably 0.75 to 0.85 mass%.
[0018]
Si: 0.20 to 1.20 mass%
Silicon Si needs to be contained in an amount of 0.20 mass% or more to serve as a deoxidizer and an element that strengthens the pearlite microstructure. The presence of more than 1.20 mass% Si promotes generation of surface defects on rails. Therefore, the Si content is 0.20 to 1.20 mass%. The Si content is preferably 0.50 to 1.00 mass%.
Si: 0.20 to 1.20 mass%
Silicon Si needs to be contained in an amount of 0.20 mass% or more to serve as a deoxidizer and an element that strengthens the pearlite microstructure. The presence of more than 1.20 mass% Si promotes generation of surface defects on rails. Therefore, the Si content is 0.20 to 1.20 mass%. The Si content is preferably 0.50 to 1.00 mass%.
[0019]
Mn: 0.20 to 1.50 mass%
Manganese Mn is an element effective for maintaining high hardness inside the rail 1 since it has an effect of lowering the pearlite transformation temperature to make the interlamellar spacing fine. With a Mn content of less than 0.20 mass%, the above effect is not enough. With a Mn content of more than 1.50 mass%, a martensite microstructure tends to be formed, and hardening and brittleness tend to occur during heat treatment and welding to degrade material properties. Further, due to Mn increasing hardenability, more bainite microstructure is formed on the surface layer Date Recue/Date Received 2022-04-06 of an internal high hardness-type rail to degrade the wear resistance. Furthermore, addition of excess Mn lowers the pearlite equilibrium transformation temperature and decreases the degree of supercooling to make the interlamellar spacing coarse. Therefore, the Mn content is 0.20 to 1.50 mass%. The Mn content is preferably 0.40 to 1.20 mass%.
Mn: 0.20 to 1.50 mass%
Manganese Mn is an element effective for maintaining high hardness inside the rail 1 since it has an effect of lowering the pearlite transformation temperature to make the interlamellar spacing fine. With a Mn content of less than 0.20 mass%, the above effect is not enough. With a Mn content of more than 1.50 mass%, a martensite microstructure tends to be formed, and hardening and brittleness tend to occur during heat treatment and welding to degrade material properties. Further, due to Mn increasing hardenability, more bainite microstructure is formed on the surface layer Date Recue/Date Received 2022-04-06 of an internal high hardness-type rail to degrade the wear resistance. Furthermore, addition of excess Mn lowers the pearlite equilibrium transformation temperature and decreases the degree of supercooling to make the interlamellar spacing coarse. Therefore, the Mn content is 0.20 to 1.50 mass%. The Mn content is preferably 0.40 to 1.20 mass%.
[0020]
P: 0.035 mass% or less The presence of more than 0.035 mass% P results in low ductility. Therefore, the P content is 0.035 mass% or less.
The P content is preferably 0.020 mass% or less. If the P
content is less than 0.001%, the steelmaking costs unavoidably increase. A P content of 0.001% or more is therefore acceptable.
P: 0.035 mass% or less The presence of more than 0.035 mass% P results in low ductility. Therefore, the P content is 0.035 mass% or less.
The P content is preferably 0.020 mass% or less. If the P
content is less than 0.001%, the steelmaking costs unavoidably increase. A P content of 0.001% or more is therefore acceptable.
[0021]
S: 0.0005 to 0.012 mass%
Sulfur S is found in a steel material mainly in the form of A type inclusions. With a S content of more than 0.012 mass%, the amount of the inclusions significantly increases, and coarse inclusions are formed at the same time, which lowers the cleanliness of the steel material.
To reduce the S content to less than 0.0005 mass%, the steelmaking costs increase. Therefore, the S content is 0.0005 to 0.012 mass%. The S content is preferably 0.0005 Date Recue/Date Received 2022-04-06 to 0.010 mass%. The S content is more preferably 0.0005 to 0.008 mass%.
S: 0.0005 to 0.012 mass%
Sulfur S is found in a steel material mainly in the form of A type inclusions. With a S content of more than 0.012 mass%, the amount of the inclusions significantly increases, and coarse inclusions are formed at the same time, which lowers the cleanliness of the steel material.
To reduce the S content to less than 0.0005 mass%, the steelmaking costs increase. Therefore, the S content is 0.0005 to 0.012 mass%. The S content is preferably 0.0005 Date Recue/Date Received 2022-04-06 to 0.010 mass%. The S content is more preferably 0.0005 to 0.008 mass%.
[0022]
Cr: 0.20 to 2.50 mass%
Chromium Cr is an element that raises the pearlite equilibrium transformation temperature to make the interlamellar spacing fine and also increases the strength through solid solution strengthening. However, enough internal hardness is not obtained with a Cr content of less than 0.20 mass%. Addition of more than 2.50 mass% Cr increases hardenability and tends to form a martensite microstructure. Moreover, under production conditions where no martensite microstructure is formed, pro-eutectoid cementite is formed at prior austenite grain boundaries. This results in low wear resistance and low fatigue damage resistance. Therefore, the Cr content is 0.20 to 2.50 mass%. The Cr content is preferably 0.60 to 1.30 mass%.
Cr: 0.20 to 2.50 mass%
Chromium Cr is an element that raises the pearlite equilibrium transformation temperature to make the interlamellar spacing fine and also increases the strength through solid solution strengthening. However, enough internal hardness is not obtained with a Cr content of less than 0.20 mass%. Addition of more than 2.50 mass% Cr increases hardenability and tends to form a martensite microstructure. Moreover, under production conditions where no martensite microstructure is formed, pro-eutectoid cementite is formed at prior austenite grain boundaries. This results in low wear resistance and low fatigue damage resistance. Therefore, the Cr content is 0.20 to 2.50 mass%. The Cr content is preferably 0.60 to 1.30 mass%.
[0023]
In addition to these composition components, the chemical composition of the rail according to the present invention may further contains one or two or more selected from Cu: 1.0 mass%
or less, Ni: 1.0 mass% or less, Nb: 0.05 mass% or less, Mo:
1.0 mass% or less, V: 0.005 to 0.10 mass%, W: 1.0 mass% or less and B: 0.005 mass% or less. The composition components will be described below separately.
In addition to these composition components, the chemical composition of the rail according to the present invention may further contains one or two or more selected from Cu: 1.0 mass%
or less, Ni: 1.0 mass% or less, Nb: 0.05 mass% or less, Mo:
1.0 mass% or less, V: 0.005 to 0.10 mass%, W: 1.0 mass% or less and B: 0.005 mass% or less. The composition components will be described below separately.
[0024]
Cu: 1.0 mass% or less Copper Cu is an element that can further strengthen the Date Recue/Date Received 2022-04-06 steel through solid solution strengthening like Cr. The presence of more than 1.0 mass% Cu tends to cause Cu cracking. Therefore, when the chemical composition contains Cu, the Cu content is preferably 1.0 mass% or less. The Cu content is more preferably 0.005 to 0.5 mass%.
Cu: 1.0 mass% or less Copper Cu is an element that can further strengthen the Date Recue/Date Received 2022-04-06 steel through solid solution strengthening like Cr. The presence of more than 1.0 mass% Cu tends to cause Cu cracking. Therefore, when the chemical composition contains Cu, the Cu content is preferably 1.0 mass% or less. The Cu content is more preferably 0.005 to 0.5 mass%.
[0025]
Ni: 1.0 mass% or less Nickel Ni is an element that can strengthen the steel without degrading the ductility. When the rail 1 contains Cu, Ni is preferably added in combination with Cu because addition of Ni can prevent or reduce Cu cracking. If the Ni content exceeds 1.0 mass%, the steel hardenability further increases, and martensite tends to be formed, which results in low fatigue damage resistance. Therefore, when Ni is contained, the Ni content is preferably 1.0 mass% or less. The Ni content is more preferably 0.005 to 0.5 mass%.
Ni: 1.0 mass% or less Nickel Ni is an element that can strengthen the steel without degrading the ductility. When the rail 1 contains Cu, Ni is preferably added in combination with Cu because addition of Ni can prevent or reduce Cu cracking. If the Ni content exceeds 1.0 mass%, the steel hardenability further increases, and martensite tends to be formed, which results in low fatigue damage resistance. Therefore, when Ni is contained, the Ni content is preferably 1.0 mass% or less. The Ni content is more preferably 0.005 to 0.5 mass%.
[0026]
Nb: 0.05 mass% or less Niobium Nb combines with C in the steel and precipitates as a carbide during and after hot rolling for forming a rail, which effectively reduces the prior austenite grain size. As a result, the wear resistance, the fatigue damage resistance, and the ductility are greatly improved to extend the service life of the rail. With a Nb content of more than 0.05 mass%, the effect of improving the wear resistance and the fatigue damage resistance is saturated, and the effect corresponding to an increase in content is not obtained. Therefore, the upper limit of the Nb Date Recue/Date Received 2022-04-06 content may be 0.05 mass%. With a Nb content of less than 0.001 mass%, it is difficult to obtain a sufficient effect of extending the service life of the rail. The presence of 0.001 mass% or more Nb provides an effect of extending the service life. Therefore, when Nb is contained, the Nb content is preferably 0.001 mass% or more. The Nb content is more preferably 0.001 mass% to 0.03 mass%.
Nb: 0.05 mass% or less Niobium Nb combines with C in the steel and precipitates as a carbide during and after hot rolling for forming a rail, which effectively reduces the prior austenite grain size. As a result, the wear resistance, the fatigue damage resistance, and the ductility are greatly improved to extend the service life of the rail. With a Nb content of more than 0.05 mass%, the effect of improving the wear resistance and the fatigue damage resistance is saturated, and the effect corresponding to an increase in content is not obtained. Therefore, the upper limit of the Nb Date Recue/Date Received 2022-04-06 content may be 0.05 mass%. With a Nb content of less than 0.001 mass%, it is difficult to obtain a sufficient effect of extending the service life of the rail. The presence of 0.001 mass% or more Nb provides an effect of extending the service life. Therefore, when Nb is contained, the Nb content is preferably 0.001 mass% or more. The Nb content is more preferably 0.001 mass% to 0.03 mass%.
[0027]
Mo: 1.0 mass% or less Molybdenum Mo is an element that can improve hardenability and can further strengthen the steel through solid solution strengthening. If the Mo content exceeds 1.0 mass%, martensite tends to be formed in the steel, which results in low wear resistance and low fatigue damage resistance. Therefore, when the chemical composition of the rail contains Mo, the Mo content is preferably 1.0 mass% or less. The Mo content is more preferably 0.005 to 0.5 mass%.
Mo: 1.0 mass% or less Molybdenum Mo is an element that can improve hardenability and can further strengthen the steel through solid solution strengthening. If the Mo content exceeds 1.0 mass%, martensite tends to be formed in the steel, which results in low wear resistance and low fatigue damage resistance. Therefore, when the chemical composition of the rail contains Mo, the Mo content is preferably 1.0 mass% or less. The Mo content is more preferably 0.005 to 0.5 mass%.
[0028]
Date Recue/Date Received 2022-04-06 V: 0.005 to 0.10 mass%
Vanadium V is an element that forms a carbonitride and is dispersedly precipitated in the matrix to improve the fatigue damage resistance and the delayed fracture resistance. With a V content of less than 0.005 mass%, the above effect is not enough. The presence of more than 0.10 mass% V results in low workability and high alloy costs and thus increases the costs for producing the rail material.
Therefore, the V content is 0.005 mass% to 0.10 mass% or less. The V content is preferably 0.01 to 0.08 mass%.
Date Recue/Date Received 2022-04-06 V: 0.005 to 0.10 mass%
Vanadium V is an element that forms a carbonitride and is dispersedly precipitated in the matrix to improve the fatigue damage resistance and the delayed fracture resistance. With a V content of less than 0.005 mass%, the above effect is not enough. The presence of more than 0.10 mass% V results in low workability and high alloy costs and thus increases the costs for producing the rail material.
Therefore, the V content is 0.005 mass% to 0.10 mass% or less. The V content is preferably 0.01 to 0.08 mass%.
[0029]
W: 1.0 mass% or less Tungsten W is an element that precipitates as a carbide during and after hot rolling for forming a rail shape and improves the strength and ductility of the rail through precipitation strengthening. If the W content exceeds 1.0 mass%, martensite is formed in the steel, resulting in low ductility. Therefore, when W is added, the W content is preferably 1.0 mass% or less. The lower limit of the W
content is not limited, but preferably 0.001 mass% or more in order to provide the effect of improving the strength and the ductility. The W content is more preferably 0.005 to 0.5 mass%.
W: 1.0 mass% or less Tungsten W is an element that precipitates as a carbide during and after hot rolling for forming a rail shape and improves the strength and ductility of the rail through precipitation strengthening. If the W content exceeds 1.0 mass%, martensite is formed in the steel, resulting in low ductility. Therefore, when W is added, the W content is preferably 1.0 mass% or less. The lower limit of the W
content is not limited, but preferably 0.001 mass% or more in order to provide the effect of improving the strength and the ductility. The W content is more preferably 0.005 to 0.5 mass%.
[0030]
B: 0.005 mass% or less Date Recue/Date Received 2022-04-06 Boron B is an element that segregates at prior austenite grain boundaries and improves hardenability to improve the strength of the rail. If the B content exceeds 0.005 mass%, a martensite microstructure is formed, resulting in low wear resistance and low fatigue damage resistance. Therefore, when B is contained, the B content is preferably 0.005 mass% or less. The lower limit of the B
content is not limited, but preferably 0.001 mass% or more in order to provide the effect of improving the strength and the ductility. The B content is more preferably 0.001 to 0.003 mass%.
B: 0.005 mass% or less Date Recue/Date Received 2022-04-06 Boron B is an element that segregates at prior austenite grain boundaries and improves hardenability to improve the strength of the rail. If the B content exceeds 0.005 mass%, a martensite microstructure is formed, resulting in low wear resistance and low fatigue damage resistance. Therefore, when B is contained, the B content is preferably 0.005 mass% or less. The lower limit of the B
content is not limited, but preferably 0.001 mass% or more in order to provide the effect of improving the strength and the ductility. The B content is more preferably 0.001 to 0.003 mass%.
[0031]
The balance other than the above composition components in the rail 1 includes Fe and incidental impurities.
Incidental impurities refer to impurities that are found in raw materials or incidentally incorporated during the production process and are basically unnecessary but allowed to be contained because they are found in trace amounts and do not affect the properties. Examples of incidental impurities include N and 0. An N content of up to 0.0080 mass% is allowable, and an 0 content of up to 0.004 mass% is allowable. Titanium Ti forms an oxide and degrades the fatigue damage resistance, which is a fundamental feature of the rail, and the Ti content is thus preferably controlled at 0.0010 mass% or less.
Date Recue/Date Received 2022-04-06
The balance other than the above composition components in the rail 1 includes Fe and incidental impurities.
Incidental impurities refer to impurities that are found in raw materials or incidentally incorporated during the production process and are basically unnecessary but allowed to be contained because they are found in trace amounts and do not affect the properties. Examples of incidental impurities include N and 0. An N content of up to 0.0080 mass% is allowable, and an 0 content of up to 0.004 mass% is allowable. Titanium Ti forms an oxide and degrades the fatigue damage resistance, which is a fundamental feature of the rail, and the Ti content is thus preferably controlled at 0.0010 mass% or less.
Date Recue/Date Received 2022-04-06
[0032]
<Steel Microstructure>
The web 3 of the rail 1 includes 95% or more area fraction of pearlite microstructure. The web 3 of the rail 1 may include trace amounts, or 5% or less in total, of bainite microstructure, martensite microstructure, pro-eutectoid cementite microstructure, and pro-eutectoid ferrite microstructure. The pearlite microstructure (pearlite blocks) is a lamellar microstructure composed of alternating layers of ferrite and cementite, and the pearlite blocks are composed of pearlite grains having the same orientation. There is a relationship between the pearlite microstructure and the crack growth, and the pearlite grain boundaries serve as a barrier to crack growth. If the web 3 includes less than 95% area fraction of pearlite microstructure, there is a shortage of pearlite grain boundaries for blocking crack growth. The web 3 of the rail 1 thus contains 95% or more area fraction of pearlite microstructure.
<Steel Microstructure>
The web 3 of the rail 1 includes 95% or more area fraction of pearlite microstructure. The web 3 of the rail 1 may include trace amounts, or 5% or less in total, of bainite microstructure, martensite microstructure, pro-eutectoid cementite microstructure, and pro-eutectoid ferrite microstructure. The pearlite microstructure (pearlite blocks) is a lamellar microstructure composed of alternating layers of ferrite and cementite, and the pearlite blocks are composed of pearlite grains having the same orientation. There is a relationship between the pearlite microstructure and the crack growth, and the pearlite grain boundaries serve as a barrier to crack growth. If the web 3 includes less than 95% area fraction of pearlite microstructure, there is a shortage of pearlite grain boundaries for blocking crack growth. The web 3 of the rail 1 thus contains 95% or more area fraction of pearlite microstructure.
[0033]
The pearlite blocks have an average size of 60 m or less. There is also a relationship between the size of the pearlite blocks and the fatigue crack growth. As described above, the pearlite grain boundaries serve as a barrier to crack growth and block crack growth. When the pearlite Date Recue/Date Received 2022-04-06 blocks have a fine size, there is a high possibility that crack growth may pass through the grain boundaries having a crack growth retardation effect. This suppresses crack growth as a result. If the pearlite blocks have an average size of more than 60 m, the crack growth retardation effect is not enough. For this, the average size of the pearlite blocks is 60 m or less, preferably 40 m or less.
The pearlite blocks have an average size of 60 m or less. There is also a relationship between the size of the pearlite blocks and the fatigue crack growth. As described above, the pearlite grain boundaries serve as a barrier to crack growth and block crack growth. When the pearlite Date Recue/Date Received 2022-04-06 blocks have a fine size, there is a high possibility that crack growth may pass through the grain boundaries having a crack growth retardation effect. This suppresses crack growth as a result. If the pearlite blocks have an average size of more than 60 m, the crack growth retardation effect is not enough. For this, the average size of the pearlite blocks is 60 m or less, preferably 40 m or less.
[0034]
<Rail Production System and Production Method>
Fig. 3 is a schematic view of an example rail production system. A rail production system 10 in Fig. 3 includes a BD (breakdown) rolling mill 11, rough rolling mills 12 and 13, a finish rolling mill 14, and a cooling facility 15. The BD rolling mill 11, the rough rolling mills 12 and 13, and the finish rolling mill 14 hot-roll a slab, and the cooling facility 15 cools the hot-rolled slab.
The finish rolling mill 14 rolls the slab through, for example, a caliber rolling process. The finish rolling mill 14 has two upper and lower rolls with grooves according to a desired cross section and directly presses the web 3, the head 4, and the foot 2. The amounts of rolling reduction of the web 3, the head 4, and the foot 2 are controlled by adjusting the shapes of the grooves in the upper and lower rolls.
<Rail Production System and Production Method>
Fig. 3 is a schematic view of an example rail production system. A rail production system 10 in Fig. 3 includes a BD (breakdown) rolling mill 11, rough rolling mills 12 and 13, a finish rolling mill 14, and a cooling facility 15. The BD rolling mill 11, the rough rolling mills 12 and 13, and the finish rolling mill 14 hot-roll a slab, and the cooling facility 15 cools the hot-rolled slab.
The finish rolling mill 14 rolls the slab through, for example, a caliber rolling process. The finish rolling mill 14 has two upper and lower rolls with grooves according to a desired cross section and directly presses the web 3, the head 4, and the foot 2. The amounts of rolling reduction of the web 3, the head 4, and the foot 2 are controlled by adjusting the shapes of the grooves in the upper and lower rolls.
[0035]
Date Recue/Date Received 2022-04-06 Next, the method for producing a rail will be described below with reference to Fig. 3. First, a slab SS (material slab) reheated in a heating furnace is rolled in the BD
(breakdown) rolling mill 11 into an approximate shape of the rail 1. The slab SS rolled in the BD rolling mill 11 is hot-rolled in the rough rolling mills 12 and 13.
Accordingly, the austenite grains coarsened by heating are repeatedly subjected to rolling and recrystallization in a recrystallization temperature range in the BD rolling mill 11 and the rough rolling mills 12 and 13 to form fine grains.
Date Recue/Date Received 2022-04-06 Next, the method for producing a rail will be described below with reference to Fig. 3. First, a slab SS (material slab) reheated in a heating furnace is rolled in the BD
(breakdown) rolling mill 11 into an approximate shape of the rail 1. The slab SS rolled in the BD rolling mill 11 is hot-rolled in the rough rolling mills 12 and 13.
Accordingly, the austenite grains coarsened by heating are repeatedly subjected to rolling and recrystallization in a recrystallization temperature range in the BD rolling mill 11 and the rough rolling mills 12 and 13 to form fine grains.
[0036]
Next, the slab SS is hot-rolled in finish rolling in the finish rolling mill 14 in such a manner that the finishing temperature of the web 3 is 1000 C or lower and the reduction in area of the web 3 is 10% or more. The finishing temperature refers to the surface temperature of the web 3 during finish rolling, but the surface temperature of the head 4 may be regarded as the finishing temperature of the web 3.
Next, the slab SS is hot-rolled in finish rolling in the finish rolling mill 14 in such a manner that the finishing temperature of the web 3 is 1000 C or lower and the reduction in area of the web 3 is 10% or more. The finishing temperature refers to the surface temperature of the web 3 during finish rolling, but the surface temperature of the head 4 may be regarded as the finishing temperature of the web 3.
[0037]
When the slab SS is rolled in a non-recrystallization temperature range (low temperature range), such as 1000 C or lower, in which recrystallization is unlikely to occur, the austenite grains are elongated without being recrystallized, Date Recue/Date Received 2022-04-06 and deformation bands are formed in the grains. During transformation from austenite to pearlite, the deformation bands in the grains serve as nucleation sites for pearlite transformation together with austenite grain boundaries.
The pearlite grains become finer accordingly. At a finishing temperature above the recrystallization temperature range, recovery by recrystallization occurs, and the average size of the pearlite blocks cannot be reduced to 60 pm or less. To make the crystal grains finer by rolling in a non-recrystallization temperature range (low temperature range), the finishing temperature during finish rolling is set to 1000 C or lower, which is a non-recrystallization temperature range (low temperature range).
If the finishing temperature is below 800 C, a significantly large load is applied to the rolls during rolling. In addition, rolling in an austenite low temperature range introduces remarkable working strain into the austenite grains, so that a desired crack growth retardation effect cannot be obtained as a result. Therefore, the finishing temperature is preferably 800 C to 900 C during finish rolling.
When the slab SS is rolled in a non-recrystallization temperature range (low temperature range), such as 1000 C or lower, in which recrystallization is unlikely to occur, the austenite grains are elongated without being recrystallized, Date Recue/Date Received 2022-04-06 and deformation bands are formed in the grains. During transformation from austenite to pearlite, the deformation bands in the grains serve as nucleation sites for pearlite transformation together with austenite grain boundaries.
The pearlite grains become finer accordingly. At a finishing temperature above the recrystallization temperature range, recovery by recrystallization occurs, and the average size of the pearlite blocks cannot be reduced to 60 pm or less. To make the crystal grains finer by rolling in a non-recrystallization temperature range (low temperature range), the finishing temperature during finish rolling is set to 1000 C or lower, which is a non-recrystallization temperature range (low temperature range).
If the finishing temperature is below 800 C, a significantly large load is applied to the rolls during rolling. In addition, rolling in an austenite low temperature range introduces remarkable working strain into the austenite grains, so that a desired crack growth retardation effect cannot be obtained as a result. Therefore, the finishing temperature is preferably 800 C to 900 C during finish rolling.
[0038]
To make the pearlite blocks finer, it is necessary to press the web 3 to induce strain. The slab SS is thus finish-rolled in the finish rolling mill 14 in such a manner Date Recue/Date Received 2022-04-06 that the reduction in area of the web 3 is 10% or more. The reduction in area is expressed by reduction in area (%) =
((Al - A2)/A1) x 100, where Al represents the cross-sectional area before finish rolling, and A2 represents the cross-sectional area after finish rolling. If the reduction in area is less than 10%, the average size of the pearlite blocks cannot be reduced to 60 m or less, and the crack growth retardation effect cannot be obtained. The reduction in area is more preferably 30% or more.
To make the pearlite blocks finer, it is necessary to press the web 3 to induce strain. The slab SS is thus finish-rolled in the finish rolling mill 14 in such a manner Date Recue/Date Received 2022-04-06 that the reduction in area of the web 3 is 10% or more. The reduction in area is expressed by reduction in area (%) =
((Al - A2)/A1) x 100, where Al represents the cross-sectional area before finish rolling, and A2 represents the cross-sectional area after finish rolling. If the reduction in area is less than 10%, the average size of the pearlite blocks cannot be reduced to 60 m or less, and the crack growth retardation effect cannot be obtained. The reduction in area is more preferably 30% or more.
[0039]
After finish rolling in the finish rolling mill 14, the web 3 of the rail is subjected to accelerated cooling in the cooling facility 15 at a cooling rate of 1 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C to 600 C. The cooling stop temperature refers to, for example, the surface temperature at a central portion of the rail web 4 measured with a radiation thermometer when cooling is stopped. The cooling rate ( C/sec) refers to a temperature change per unit time (sec) from cooling start to cooling stop.
After finish rolling in the finish rolling mill 14, the web 3 of the rail is subjected to accelerated cooling in the cooling facility 15 at a cooling rate of 1 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C to 600 C. The cooling stop temperature refers to, for example, the surface temperature at a central portion of the rail web 4 measured with a radiation thermometer when cooling is stopped. The cooling rate ( C/sec) refers to a temperature change per unit time (sec) from cooling start to cooling stop.
[0040]
At a cooling rate higher than 5 C/s, the area fraction of pearlite microstructure decreases and the area fraction of martensite microstructure and other microstructures Date Recue/Date Received 2022-04-06 increases, so that the pearlite microstructure cannot occupy 95% or more area fraction. Accelerated cooling at a cooling rate of 1 to 5 C/s can form the web 3 composed of pearlite and containing 95% or more area fraction of pearlite microstructure. In addition, the production efficiency can be improved because there is no need to maintain the temperature until bainite transformation starts unlike a conventional manner.
At a cooling rate higher than 5 C/s, the area fraction of pearlite microstructure decreases and the area fraction of martensite microstructure and other microstructures Date Recue/Date Received 2022-04-06 increases, so that the pearlite microstructure cannot occupy 95% or more area fraction. Accelerated cooling at a cooling rate of 1 to 5 C/s can form the web 3 composed of pearlite and containing 95% or more area fraction of pearlite microstructure. In addition, the production efficiency can be improved because there is no need to maintain the temperature until bainite transformation starts unlike a conventional manner.
[0041]
The structure and operational effects of the present invention will be more specifically described below by way of Example. The present invention is not limited by the following Example and can be appropriately modified within the range of the spirit of the present invention. All of the modifications are included in the technical scope of the present invention.
The structure and operational effects of the present invention will be more specifically described below by way of Example. The present invention is not limited by the following Example and can be appropriately modified within the range of the spirit of the present invention. All of the modifications are included in the technical scope of the present invention.
[0042]
<Preparation of Test Specimens>
First, steels Al to A15 and Bl to B6, which have different chemical compositions, are prepared. Table 1 below shows the components of the steels Al to A15 and Bl to B6. The blanks in Table 1 mean that the component is absent or negligible because of the content being in the range of incidental impurities.
Date Recue/Date Received 2022-04-06 [ 0 0 4 3 ]
Date Recue/Date Received 2022-04-06 [Table 1]
Chemical Composition (mass%) Steel No. Note C Si Mn P S Cr Cu Ni Nb Mo V W B
Al 0.71 0.81 0.63 0.014 0.004 1.35 Invention Example A2 0.82 0.65 1.02 0.011 0.006 1.15 Invention Example A3 0.94 0.23 0.92 0.011 0.012 0.95 Invention Example ..... ....
A4 0.99 0.58 0.24 0.010 0.005 0.35 Invention Example A5 1.08 1.05 0.78 0.010 0.010 0.57 Invention Example A6 1.12 1.16 0.42 0.010 0.009 1.03 Invention Example Al 1.18 0.77 1.46 0.010Ø005_0.21 Invention Example B1 0.65 0.42 1.15 0.014 0.008 0.40 Comparative Example B2 1.22 0.84 0.86 0.014 0.005 1.51 Comparative Example.
B3 1.01 0.18 0.24 0.012 0.006 0.65 Comparative Example 84 0.83 0.63 1.53 0.011 0.011 0.60 __________________________ Comparative Example B5 0.75 0.77 1.42 0.014 0.010 0.19 Comparative Example A8 0.81 0.75 0.68 0.015 0.005 1.23 0.89 Invention Example A9 1.03 0.66 1.01 0.012 0.006 1.06 0.85 Invention Example A10 1.10 0.25 0.94 0.013 0.003 0.93 0.04 Invention Example All 1.18 0.53 0.21 0.009 0.004 0.36 0.82 0.76 Invention Example . .
Al2 0.75 0.93 0.44 0.014 0.005 0.45 0.08 Invention Example A13 0.92 0.31 0.63 0.012 0.011 0.64 0.77 0.91 Invention Example A14 0.85Ø78 0.84 0.011 0.009 0.87 Ø03. 0.004 Invention Example A15 0.84Ø25 0.21 0.010 0.005 2.49 Invention Example B6 0.91 0.56 0.36 0.011 0.008 2.52 Comparative Example [0044]
Next, rails (No. 1 to No. 25 in Table 2 below) were produced in the rail production system 10 in Fig. 3 under predetermined production conditions using the steels Al to A15 and 31 to B6 containing the composition components in Table 1. Subsequently, steel materials were extracted from the webs 3 of the produced rails 1 to prepare test specimens. Fig. 4 is a schematic view of an example test Date Recue/Date Received 2022-04-06 specimen. In Fig. 4, the test specimen has, for example, a plate shape with width W = 20 mm, height H = 100 mm, and thickness B - 5 mm. The test specimen has a notch at a half H/2 of the height H. The notch has length L = 2 mm and width C - 0.2 mm. The end of the notch has curvature radius R =
0.1 mm.
[0045]
Table 2 shows the rail production conditions and the test results.
[0046]
Date Recue/Date Received 2022-04-06 [Table 2]
Production Conditions Rail Steel Web Microstructure Block Size Crack Growth Rate da/dN
No. No. Reduction(%) in Area of Web Web Cooling *1 ( m) at AK = 20 MPa= MI/2 (X 10-8 m/cycle) Note at 1000 C or Lower Rate( C/sec) 7.7 Invention Example 5.2 Invention Example 6.5 Invention Example , 3.1 , Invention Example .
A5-1 15 2 P 52 7.9 , Invention Example .
4.8 Invention Example 3.8 Invention Example 8 A1-2 ____ 5 3 P 68 8.2 Comparative Example 9.2 Comparative Example -A4-2 25 6 P + M 50 10.3 Comparative Example .
w 8.9 Comparative Example tzal .,,., 11.2 Comparative Example 13 B2-1 15 4 P + 0 30 12.1 Comparative Example 2 14 B3-1 20 3 . P 25 8.5 Comparative Example i B4-1 ___ 35 2 - P + M 31 9.4 Comparative Example , g 9.1 Comparative Example 17 A8-1 ___ 12 3 P 55 6.9 Invention Example , 5.6 Invention Example 6.0 Invention Example , A11-1 42 3 - P 17 4.2 Invention Example 21 Al2-1 18 4 P 52 7.8 . Invention Example , 5.5 Invention Example 4.9 Invention Example 24 A15-1 . 25 . 2 P 45 6.8 I Invention Example B6-1 20 1 P + 0 39 10.9 I Comparative Example *1: Microstructure: P ¨> pearlite, M ¨> martensite, 0 ¨> cementite indicates that the area fraction of pearlite is 95% or more, and "P + M" and "P + 0" indicate that the area fraction of pearlite is less than 95%.
Date Recue/Date Received 2022-04-06 [0047]
<Evaluation Method>
A fatigue crack growth test was conducted at a stress ratio R = 0.1 using the test specimen in Fig. 4, and the fatigue crack growth rate da/dN (m/cycle) was measured at a stress intensity factor AK - 20 MPa=M1/2 to evaluate the surface damage resistance of the web. When the fatigue crack growth rate was 8.0 x 10-8 or less, the web was determined to have crack growth resistance.
[0048]
In the production conditions in Table 2, the finishing temperature is obtained by measuring the surface temperature of the web 3 at the inlet of the finish rolling mill 14 using a radiation thermometer, and the cooling stop temperature is obtained by measuring the surface temperature of the web 3 using a radiation thermometer when cooling is stopped.
[0049]
The size of the pearlite blocks in Table 2 was obtained as follows: a test specimen for microscopic observation of L
cross sections was sampled at a middle point of the rail web, embedded followed by mirror polishing, and then subjected to orientation analysis using an EBSD (electron backscatter diffraction pattern), and the sizes of pearlite grains of respective orientations were measured as Date Recue/Date Received 2022-04-06 equivalent circular diameters and averaged. The grain boundaries at which a difference in orientation between adjacent crystal orientations was 50 or more were determined to define different pearlite blocks. The measurement region was 300 m square, the step size was 0.3 m, and measurement points at which the Confidence index indicating the reliability of measured orientation was 0.1 or less were removed from analysis targets. Crystal grains on the edges of the measurement region were also removed from analysis targets.
[0050]
In Table 2, "P" means that the web includes 95% or more area fraction of pearlite microstructure, and trace amounts, or 5% or less in total, of bainite microstructure, martensite microstructure, pro-eutectoid cementite microstructure, and pro-eutectoid ferrite microstructure.
The area fraction of pearlite microstructure can be measured by using a known technique. For example, the sampled test specimen is polished and then etched in nital, the type of microstructure is identified through cross-sectional observation using an optical microscope at a magnification of 400 times, and the area fraction of pearlite microstructure is calculated by image analysis.
[0051]
Rails No. 1 to No. 7 and No. 24 were produced by using Date Recue/Date Received 2022-04-06 compatible steels that satisfy the mass percentages of the component composition of the present invention in accordance with production methods that satisfy the finish rolling conditions and the cooling conditions. The area fraction of pearlite in each of the webs 3 was 95% or more, and the average size of pearlite blocks was 60 m or less. As a result, the crack growth rate da/dN (m/cycle) in each of the webs 3 at a stress intensity factor AK = 20 MPa=m1/2 was 8.0 x 10-8 or less. In addition, the crack growth rate da/dN
(m/cycle) in the web 3 was 8.0 x 10-8 or less even when a predetermined mass% of at least one of Cu, Ni, Nb, Mo, V, W, and B was contained as in No. 17 to No. 23 (Steel No. A8 to No. A14).
[0052]
When the reduction in area in finish rolling is less than 10% as in No. 8 and No. 9, the average size of pearlite blocks is larger than 60 RM. As a result, the crack growth rate da/dN (m/cycle) in the web 3 does not satisfy 8.0 x 10-8 or less.
[0053]
When the cooling rate after finish rolling is higher than 5 C/sec as in No. 10, the area fraction of martensite microstructure is high, and the area fraction of pearlite microstructure in the web 3 is less than 95%. As a result, the crack growth rate da/dN (m/cycle) in the web 3 does not Date Recue/Date Received 2022-04-06 satisfy 8.0 x 10-8 or less.
[0054]
When, as in No. 11 to No. 16 and No. 25, steels are out of the range of the mass percentages of the chemical composition according to the present invention, even when the temperature conditions and the reduction in area in finish rolling and the cooling rate satisfy the conditions defined in the present invention, the area fraction of pearlite microstructure in the web 3 is less than 95%, or the average size of pearlite blocks is larger than 60 um.
As a result, the crack growth rate da/dN (m/cycle) in the web does not satisfy 8.0 x 10-8 or less.
[0055]
According to the present invention, the microstructure of the web 3 of the rail 1 is controlled by controlling the components of the steel, the finish rolling conditions, and the cooling conditions to lower the web crack growth rate in the web 3 of the rail 1 and thus to suppress the crack growth in the web 3 and the breakage of the rail.
[0056]
The embodiment of the present invention is not limited to the above embodiment, and various modifications can be made to the embodiment of the present invention. For example, the conditions for producing the web 3 are illustrated in the embodiment, in which the foot 2 and the Date Recue/Date Received 2022-04-06 head 4 are hot-rolled at the same time when the web 3 is hot-rolled. There, for example, a rail 1 may be produced by preparing a slab having chemical compositions that satisfy the performance requirements for both the web 3 and the head 4, and hot rolling and cooling the web 3 and the head 4 under different conditions such that both the crack growth resistance of the web 3 and the wear resistance of the head 4 and other properties are satisfied.
Reference Signs List [0057]
1 Rail 2 Foot (bottom) 3 Web 4 Head Rail production system 11 BD rolling mill 12, 13 Rough rolling mill 14 Finish rolling mill Cooling facility SS Slab Date Recue/Date Received 2022-04-06
<Preparation of Test Specimens>
First, steels Al to A15 and Bl to B6, which have different chemical compositions, are prepared. Table 1 below shows the components of the steels Al to A15 and Bl to B6. The blanks in Table 1 mean that the component is absent or negligible because of the content being in the range of incidental impurities.
Date Recue/Date Received 2022-04-06 [ 0 0 4 3 ]
Date Recue/Date Received 2022-04-06 [Table 1]
Chemical Composition (mass%) Steel No. Note C Si Mn P S Cr Cu Ni Nb Mo V W B
Al 0.71 0.81 0.63 0.014 0.004 1.35 Invention Example A2 0.82 0.65 1.02 0.011 0.006 1.15 Invention Example A3 0.94 0.23 0.92 0.011 0.012 0.95 Invention Example ..... ....
A4 0.99 0.58 0.24 0.010 0.005 0.35 Invention Example A5 1.08 1.05 0.78 0.010 0.010 0.57 Invention Example A6 1.12 1.16 0.42 0.010 0.009 1.03 Invention Example Al 1.18 0.77 1.46 0.010Ø005_0.21 Invention Example B1 0.65 0.42 1.15 0.014 0.008 0.40 Comparative Example B2 1.22 0.84 0.86 0.014 0.005 1.51 Comparative Example.
B3 1.01 0.18 0.24 0.012 0.006 0.65 Comparative Example 84 0.83 0.63 1.53 0.011 0.011 0.60 __________________________ Comparative Example B5 0.75 0.77 1.42 0.014 0.010 0.19 Comparative Example A8 0.81 0.75 0.68 0.015 0.005 1.23 0.89 Invention Example A9 1.03 0.66 1.01 0.012 0.006 1.06 0.85 Invention Example A10 1.10 0.25 0.94 0.013 0.003 0.93 0.04 Invention Example All 1.18 0.53 0.21 0.009 0.004 0.36 0.82 0.76 Invention Example . .
Al2 0.75 0.93 0.44 0.014 0.005 0.45 0.08 Invention Example A13 0.92 0.31 0.63 0.012 0.011 0.64 0.77 0.91 Invention Example A14 0.85Ø78 0.84 0.011 0.009 0.87 Ø03. 0.004 Invention Example A15 0.84Ø25 0.21 0.010 0.005 2.49 Invention Example B6 0.91 0.56 0.36 0.011 0.008 2.52 Comparative Example [0044]
Next, rails (No. 1 to No. 25 in Table 2 below) were produced in the rail production system 10 in Fig. 3 under predetermined production conditions using the steels Al to A15 and 31 to B6 containing the composition components in Table 1. Subsequently, steel materials were extracted from the webs 3 of the produced rails 1 to prepare test specimens. Fig. 4 is a schematic view of an example test Date Recue/Date Received 2022-04-06 specimen. In Fig. 4, the test specimen has, for example, a plate shape with width W = 20 mm, height H = 100 mm, and thickness B - 5 mm. The test specimen has a notch at a half H/2 of the height H. The notch has length L = 2 mm and width C - 0.2 mm. The end of the notch has curvature radius R =
0.1 mm.
[0045]
Table 2 shows the rail production conditions and the test results.
[0046]
Date Recue/Date Received 2022-04-06 [Table 2]
Production Conditions Rail Steel Web Microstructure Block Size Crack Growth Rate da/dN
No. No. Reduction(%) in Area of Web Web Cooling *1 ( m) at AK = 20 MPa= MI/2 (X 10-8 m/cycle) Note at 1000 C or Lower Rate( C/sec) 7.7 Invention Example 5.2 Invention Example 6.5 Invention Example , 3.1 , Invention Example .
A5-1 15 2 P 52 7.9 , Invention Example .
4.8 Invention Example 3.8 Invention Example 8 A1-2 ____ 5 3 P 68 8.2 Comparative Example 9.2 Comparative Example -A4-2 25 6 P + M 50 10.3 Comparative Example .
w 8.9 Comparative Example tzal .,,., 11.2 Comparative Example 13 B2-1 15 4 P + 0 30 12.1 Comparative Example 2 14 B3-1 20 3 . P 25 8.5 Comparative Example i B4-1 ___ 35 2 - P + M 31 9.4 Comparative Example , g 9.1 Comparative Example 17 A8-1 ___ 12 3 P 55 6.9 Invention Example , 5.6 Invention Example 6.0 Invention Example , A11-1 42 3 - P 17 4.2 Invention Example 21 Al2-1 18 4 P 52 7.8 . Invention Example , 5.5 Invention Example 4.9 Invention Example 24 A15-1 . 25 . 2 P 45 6.8 I Invention Example B6-1 20 1 P + 0 39 10.9 I Comparative Example *1: Microstructure: P ¨> pearlite, M ¨> martensite, 0 ¨> cementite indicates that the area fraction of pearlite is 95% or more, and "P + M" and "P + 0" indicate that the area fraction of pearlite is less than 95%.
Date Recue/Date Received 2022-04-06 [0047]
<Evaluation Method>
A fatigue crack growth test was conducted at a stress ratio R = 0.1 using the test specimen in Fig. 4, and the fatigue crack growth rate da/dN (m/cycle) was measured at a stress intensity factor AK - 20 MPa=M1/2 to evaluate the surface damage resistance of the web. When the fatigue crack growth rate was 8.0 x 10-8 or less, the web was determined to have crack growth resistance.
[0048]
In the production conditions in Table 2, the finishing temperature is obtained by measuring the surface temperature of the web 3 at the inlet of the finish rolling mill 14 using a radiation thermometer, and the cooling stop temperature is obtained by measuring the surface temperature of the web 3 using a radiation thermometer when cooling is stopped.
[0049]
The size of the pearlite blocks in Table 2 was obtained as follows: a test specimen for microscopic observation of L
cross sections was sampled at a middle point of the rail web, embedded followed by mirror polishing, and then subjected to orientation analysis using an EBSD (electron backscatter diffraction pattern), and the sizes of pearlite grains of respective orientations were measured as Date Recue/Date Received 2022-04-06 equivalent circular diameters and averaged. The grain boundaries at which a difference in orientation between adjacent crystal orientations was 50 or more were determined to define different pearlite blocks. The measurement region was 300 m square, the step size was 0.3 m, and measurement points at which the Confidence index indicating the reliability of measured orientation was 0.1 or less were removed from analysis targets. Crystal grains on the edges of the measurement region were also removed from analysis targets.
[0050]
In Table 2, "P" means that the web includes 95% or more area fraction of pearlite microstructure, and trace amounts, or 5% or less in total, of bainite microstructure, martensite microstructure, pro-eutectoid cementite microstructure, and pro-eutectoid ferrite microstructure.
The area fraction of pearlite microstructure can be measured by using a known technique. For example, the sampled test specimen is polished and then etched in nital, the type of microstructure is identified through cross-sectional observation using an optical microscope at a magnification of 400 times, and the area fraction of pearlite microstructure is calculated by image analysis.
[0051]
Rails No. 1 to No. 7 and No. 24 were produced by using Date Recue/Date Received 2022-04-06 compatible steels that satisfy the mass percentages of the component composition of the present invention in accordance with production methods that satisfy the finish rolling conditions and the cooling conditions. The area fraction of pearlite in each of the webs 3 was 95% or more, and the average size of pearlite blocks was 60 m or less. As a result, the crack growth rate da/dN (m/cycle) in each of the webs 3 at a stress intensity factor AK = 20 MPa=m1/2 was 8.0 x 10-8 or less. In addition, the crack growth rate da/dN
(m/cycle) in the web 3 was 8.0 x 10-8 or less even when a predetermined mass% of at least one of Cu, Ni, Nb, Mo, V, W, and B was contained as in No. 17 to No. 23 (Steel No. A8 to No. A14).
[0052]
When the reduction in area in finish rolling is less than 10% as in No. 8 and No. 9, the average size of pearlite blocks is larger than 60 RM. As a result, the crack growth rate da/dN (m/cycle) in the web 3 does not satisfy 8.0 x 10-8 or less.
[0053]
When the cooling rate after finish rolling is higher than 5 C/sec as in No. 10, the area fraction of martensite microstructure is high, and the area fraction of pearlite microstructure in the web 3 is less than 95%. As a result, the crack growth rate da/dN (m/cycle) in the web 3 does not Date Recue/Date Received 2022-04-06 satisfy 8.0 x 10-8 or less.
[0054]
When, as in No. 11 to No. 16 and No. 25, steels are out of the range of the mass percentages of the chemical composition according to the present invention, even when the temperature conditions and the reduction in area in finish rolling and the cooling rate satisfy the conditions defined in the present invention, the area fraction of pearlite microstructure in the web 3 is less than 95%, or the average size of pearlite blocks is larger than 60 um.
As a result, the crack growth rate da/dN (m/cycle) in the web does not satisfy 8.0 x 10-8 or less.
[0055]
According to the present invention, the microstructure of the web 3 of the rail 1 is controlled by controlling the components of the steel, the finish rolling conditions, and the cooling conditions to lower the web crack growth rate in the web 3 of the rail 1 and thus to suppress the crack growth in the web 3 and the breakage of the rail.
[0056]
The embodiment of the present invention is not limited to the above embodiment, and various modifications can be made to the embodiment of the present invention. For example, the conditions for producing the web 3 are illustrated in the embodiment, in which the foot 2 and the Date Recue/Date Received 2022-04-06 head 4 are hot-rolled at the same time when the web 3 is hot-rolled. There, for example, a rail 1 may be produced by preparing a slab having chemical compositions that satisfy the performance requirements for both the web 3 and the head 4, and hot rolling and cooling the web 3 and the head 4 under different conditions such that both the crack growth resistance of the web 3 and the wear resistance of the head 4 and other properties are satisfied.
Reference Signs List [0057]
1 Rail 2 Foot (bottom) 3 Web 4 Head Rail production system 11 BD rolling mill 12, 13 Rough rolling mill 14 Finish rolling mill Cooling facility SS Slab Date Recue/Date Received 2022-04-06
Claims (5)
- [Claim 1]
A rail comprising a foot, a web, and a head, wherein the web has a chemical composition comprising:
C: 0.70 to 1.20 mass%, Si: 0.20 to 1.20 mass%, Mn: 0.20 to 1.50 mass%, P: 0.035 mass% or less, S: 0.0005 to 0.012 mass%, and Cr: 0.20 to 2.50 mass%, with the balance being Fe and incidental impurities, an area fraction of pearlite in the web is 95% or more, and an average size of pearlite blocks is 30 pm or less. - [Claim 2]
The rail according to Claim 1, wherein the chemical composition further comprises one or two or more selected from Cu: 1.0 mass% or less, Ni: 1.0 mass% or less, Nb: 0.05 mass% or less, Mo: 1.0 mass% or less, V: 0.005 to 0.10 mass%, W: 1.0 mass% or less and B: 0.005 mass% or less. - [Claim 3]
The rail according to Claim 1 or 2, wherein a crack growth rate da/dN (m/cycle) in the web at a stress intensity factor AK --= 20 MPa.m1/2 is 8.0 x 10-8 or less. - [Claim 4]
A rail production method for producing the rail according to any one of Claims 1 to 3 from a slab having the chemical composition, the method comprising:
performing finish rolling at a finishing temperature of Date Recue/Date Received 2023-06-01 1000 C or lower in such a manner that a reduction in area of a web is 10% or more; and after finish rolling, cooling the web at a cooling rate of 1 to 5 C/s from a temperature higher than or equal to a pearlite transformation start temperature to a temperature range of 400 C
to 600 C. - [Claim 5]
The rail production method according to Claim 4, wherein the finishing temperature in finish-rolling the web is in a range of 800 to 900 C.
Date Recue/Date Received 2023-06-01
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2019-187316 | 2019-10-11 | ||
JP2019187316 | 2019-10-11 | ||
PCT/JP2020/028616 WO2021070452A1 (en) | 2019-10-11 | 2020-07-27 | Rail and method for manufacturing same |
Publications (2)
Publication Number | Publication Date |
---|---|
CA3157401A1 CA3157401A1 (en) | 2021-04-15 |
CA3157401C true CA3157401C (en) | 2024-04-09 |
Family
ID=75437831
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CA3157401A Active CA3157401C (en) | 2019-10-11 | 2020-07-27 | Rail and method for producing the same |
Country Status (7)
Country | Link |
---|---|
US (1) | US20230250505A1 (en) |
EP (1) | EP4023777A4 (en) |
JP (1) | JP7063400B2 (en) |
CN (1) | CN114502761B (en) |
AU (1) | AU2020364505B2 (en) |
CA (1) | CA3157401C (en) |
WO (1) | WO2021070452A1 (en) |
Family Cites Families (26)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5947326A (en) | 1982-09-13 | 1984-03-17 | Nippon Steel Corp | Production of rail having excellent resistance to edge rupture |
JPS6299438A (en) | 1985-10-24 | 1987-05-08 | Nippon Kokan Kk <Nkk> | Wear-resistant high-efficiency rail having instable fracture propagation stopping capacity |
JP3081116B2 (en) | 1994-10-07 | 2000-08-28 | 新日本製鐵株式会社 | High wear resistant rail with pearlite metal structure |
US5658400A (en) * | 1993-12-20 | 1997-08-19 | Nippon Steel Corporation | Rails of pearlitic steel with high wear resistance and toughness and their manufacturing methods |
JPH08109440A (en) * | 1994-10-07 | 1996-04-30 | Nippon Steel Corp | High toughness rail with pearlitic metallic structure |
JP3078461B2 (en) | 1994-11-15 | 2000-08-21 | 新日本製鐵株式会社 | High wear-resistant perlite rail |
JPH08246100A (en) | 1995-03-07 | 1996-09-24 | Nippon Steel Corp | Pearlitic rail excellent in wear resistance and its production |
JPH08246101A (en) | 1995-03-07 | 1996-09-24 | Nippon Steel Corp | Pearlitic rail excellent in wear resistance and damage resistance and its production |
JPH10195601A (en) | 1996-12-27 | 1998-07-28 | Nippon Steel Corp | Pearlitic steel rail excellent in wear resistance and internal fatigue fracture resistance and manufacture therefor |
JP2001234238A (en) * | 2000-02-18 | 2001-08-28 | Nippon Steel Corp | Producing method for highly wear resistant and high toughness rail |
JP4598265B2 (en) | 2000-06-14 | 2010-12-15 | 新日本製鐵株式会社 | Perlite rail and its manufacturing method |
JP3769218B2 (en) * | 2001-04-04 | 2006-04-19 | 新日本製鐵株式会社 | Low segregation pearlite rail with excellent wear resistance and ductility |
JP2004043863A (en) * | 2002-07-10 | 2004-02-12 | Nippon Steel Corp | Rail having reduced amount of pro-eutectoid cementite structure formed in rail column section |
BRPI0304718B1 (en) * | 2002-04-05 | 2016-01-12 | Nippon Steel & Sumitomo Metal Corp | method for producing an excellent perlite steel rail for wear resistance and ductility |
JP4272385B2 (en) * | 2002-04-05 | 2009-06-03 | 新日本製鐵株式会社 | Perlite rail with excellent wear resistance and ductility |
JP4272410B2 (en) * | 2002-11-12 | 2009-06-03 | 新日本製鐵株式会社 | Heat treatment method for pearlite rail |
JP4214043B2 (en) * | 2003-12-01 | 2009-01-28 | 新日本製鐵株式会社 | Method for producing high carbon steel rails with excellent wear resistance and ductility |
JP4736790B2 (en) * | 2005-12-22 | 2011-07-27 | Jfeスチール株式会社 | High-strength pearlite rail and manufacturing method thereof |
JP5145795B2 (en) * | 2006-07-24 | 2013-02-20 | 新日鐵住金株式会社 | Method for producing pearlitic rails with excellent wear resistance and ductility |
JP5472418B2 (en) * | 2006-07-24 | 2014-04-16 | 新日鐵住金株式会社 | Method for producing pearlitic rails with excellent wear resistance and ductility |
JP5282506B2 (en) * | 2008-09-25 | 2013-09-04 | Jfeスチール株式会社 | Internal high hardness type pearlitic steel rail with excellent wear resistance and fatigue damage resistance and method for manufacturing the same |
EP2447383B1 (en) * | 2009-06-26 | 2018-12-19 | Nippon Steel & Sumitomo Metal Corporation | Pearlite based high-carbon steel rail having excellent ductility and process for production thereof |
AU2012378562B2 (en) * | 2012-04-25 | 2016-07-07 | Jfe Steel Corporation | Pearlite rail, flash butt welding method for pearlite rail, and method for manufacturing pearlite rail |
JP6137043B2 (en) * | 2014-04-30 | 2017-05-31 | Jfeスチール株式会社 | Rail manufacturing method |
CN104561816B (en) * | 2015-01-07 | 2016-08-31 | 攀钢集团攀枝花钢铁研究院有限公司 | The rail of a kind of high-strength, fatigue-resistant function admirable and production method thereof |
CN109023058B (en) * | 2018-08-27 | 2020-06-30 | 攀钢集团攀枝花钢铁研究院有限公司 | Oxide film, corrosion-resistant steel rail and preparation method of steel rail |
-
2020
- 2020-07-27 CA CA3157401A patent/CA3157401C/en active Active
- 2020-07-27 AU AU2020364505A patent/AU2020364505B2/en active Active
- 2020-07-27 CN CN202080070379.7A patent/CN114502761B/en active Active
- 2020-07-27 WO PCT/JP2020/028616 patent/WO2021070452A1/en unknown
- 2020-07-27 US US17/766,390 patent/US20230250505A1/en active Pending
- 2020-07-27 EP EP20874591.9A patent/EP4023777A4/en active Pending
- 2020-07-27 JP JP2020558653A patent/JP7063400B2/en active Active
Also Published As
Publication number | Publication date |
---|---|
EP4023777A4 (en) | 2023-03-01 |
EP4023777A1 (en) | 2022-07-06 |
CA3157401A1 (en) | 2021-04-15 |
JP7063400B2 (en) | 2022-05-09 |
CN114502761A (en) | 2022-05-13 |
US20230250505A1 (en) | 2023-08-10 |
AU2020364505A1 (en) | 2022-04-28 |
CN114502761B (en) | 2024-01-09 |
WO2021070452A1 (en) | 2021-04-15 |
JPWO2021070452A1 (en) | 2021-10-21 |
AU2020364505B2 (en) | 2023-08-03 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US10253397B2 (en) | Pearlitic rail and method for manufacturing pearlitic rail | |
JP7018510B2 (en) | Wear-resistant steel with excellent hardness and impact toughness and its manufacturing method | |
EP1178126A1 (en) | Bar or wire product for use in cold forging and method for producing the same | |
RU2488643C1 (en) | Rail from high-carbon pearlite steel with excellent ductility, and method for its obtaining | |
EP3719149B1 (en) | High-hardness steel product and method of manufacturing the same | |
KR20150013891A (en) | Steel material | |
RU2676374C1 (en) | Rail | |
US20090250146A1 (en) | High Strength Thick-Gauge Electric-Resistance Welded Steel Pipe Excellent in Hardenability, Hot Workability and Fatigue Strength and Method of Production of the Same | |
KR101657017B1 (en) | Steel material | |
EP3717142B1 (en) | Method for manufacturing a rail and corresponding rail | |
US20220033927A1 (en) | Hot rolled steel sheet and method for producing same | |
JP6769579B2 (en) | Rails and their manufacturing methods | |
CN113966406B (en) | Steel rail and method for manufacturing same | |
CA3157401C (en) | Rail and method for producing the same | |
US11819909B2 (en) | Method for manufacturing high-manganese steel cast slab and method for manufacturing high-manganese steel slab or steel sheet | |
CN113557312B (en) | Rail for railway vehicle | |
JP2021021139A (en) | Wear-resistant steel plate and method for producing the same | |
WO2022004247A1 (en) | Rail having excellent fatigue crack propagation resistance characteristics, and method for producing same | |
EP3901306B1 (en) | Structural steel having excellent brittle fracture resistance and method for manufacturing same | |
CA3094157C (en) | Rail and method for manufacturing same |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |
|
EEER | Examination request |
Effective date: 20220406 |