CN111235487A - Steel for long-life drill rod and production method thereof - Google Patents
Steel for long-life drill rod and production method thereof Download PDFInfo
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- CN111235487A CN111235487A CN202010208518.XA CN202010208518A CN111235487A CN 111235487 A CN111235487 A CN 111235487A CN 202010208518 A CN202010208518 A CN 202010208518A CN 111235487 A CN111235487 A CN 111235487A
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- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
Abstract
The invention provides a long-life drill rod steel and a production method thereof, wherein the long-life drill rod steel comprises the following chemical components: 0.60-0.70%, Si: 0.40-0.60%, Mn: 0.70-0.90%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent, Mo: 0.30-0.40%, Ni: 0.15-0.30%, Cr: 0.20-0.30%, Als: 0.015-0.040%, the rest is iron and inevitable impurities. The production method comprises the following steps: electric arc furnace smelting → LF furnace refining → RH vacuum degassing → round billet continuous casting → heating of casting blank heating furnace → cogging → six-stand continuous rolling mill rolling. Compared with the prior art, the production process of the two-fire finished product combines the Cr, Ni and Mo composite alloying principle, the high-strength high-toughness long-life drill rod steel is developed, and the service life is prolonged by 30-40%.
Description
Technical Field
The invention belongs to the field of steel, and particularly relates to long-life drill rod steel and a production method thereof.
Background
The quality of the hollow steel is a main raw material for manufacturing the rock drill rod, the service life of the drill rod is directly influenced, and with the improvement of the mechanization degree of mining equipment and the trend of the development of rock drilling machines towards large-scale, hydraulic and high-speed, the impact load born by the drill rod made of the hollow steel is continuously increased.
In addition, the high-power rock drill is widely adopted along with domestic construction sites. Higher requirements are put on the quality of the connecting drill rod used in a matching way, and particularly the service life under the high-temperature condition is higher and higher. The existing commonly used 55SiMnMo steel bears the impact load action of high peak value and high frequency in the rock drilling process, so that the rapid fatigue failure is caused. In addition, the drill tool is also subjected to various composite stresses such as torsion, bending, stretching, compression and the like, and is subjected to the corrosion and erosion effects of working media such as rocks, rock dust, mineral water and the like in the environment of high-speed rotation and collision, so that the requirements on the internal quality and the surface quality of steel are high.
In addition, the common production process in the hollow steel raw material of the drill tool comprises the following steps: electric arc furnace (or converter) smelting → LF furnace refining → billet continuous casting, because the control of segregation, shrinkage cavity, looseness and the like of the alloy elements of the traditional continuous casting billet is poor, the hardness of the final drill rod is not uniform, and the service life is reduced.
Disclosure of Invention
The invention aims to provide a long-life steel for a drill rod.
The invention also aims to provide a production method of the steel for the long-life drill rod, which adopts the production process of smelting in an electric arc furnace → refining in an LF furnace → RH vacuum degassing → round billet continuous casting → heating in a casting blank heating furnace → cogging → rolling in a six-stand continuous rolling mill, combines the Ni, Cr and Mo composite alloying principle to produce the steel for the long-life drill rod, and improves the service life of the steel for the long-life drill rod by 30-40 percent compared with the service life of a rock drilling drill rod made of continuous casting small square billets with the same specification by adopting the technical scheme.
The specific technical scheme of the invention is as follows:
the steel for the long-life drill rod comprises the following chemical components in percentage by mass: c: 0.60-0.70%, Si: 0.40-0.60%, Mn: 0.70-0.90%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent, Mo: 0.30-0.40%, Ni: 0.15-0.30%, Cr: 0.20-0.30%, Als: 0.015-0.040%, the rest is iron and inevitable impurities.
The functions and the proportion of the elements are as follows:
c: the element C is necessary for obtaining high strength and hardness. Although the high C content is beneficial to the strength, the hardness and the like of steel, the drill rod is in a severe use environment and is generally used in mining of mines, and the requirement of sufficient hardness of the drill rod needs to be ensured, so that the C content is controlled to be 0.60-0.70%.
Si: si is a main deoxidizing element in steel, has a strong solid solution strengthening effect, increases the content of Si, enables the brazing tool not to easily generate austenite phase transformation and martensite transformation when being heated and cooled, and is beneficial to improving the heat damage resistance of the brazing tool raw material, but the excessive Si can increase the heat sensitivity and the brittleness of the material. Therefore, the Si content is controlled to be 0.40-0.60%.
Mn: mn is an effective element for deoxidation and desulfurization, and can also improve the hardenability and strength of steel, and when the content is less than 0.50%, the above-mentioned effect is difficult to be achieved. However, Mn and P have strong tendency of grain boundary co-segregation during tempering of quenched steel, promote temper brittleness and deteriorate toughness of steel, so that the Mn content is controlled to be 0.70-0.90%.
Cr: cr can effectively improve the hardenability and the tempering resistance of the steel so as to obtain the required high strength and improve the friction and wear resistance of the steel; however, since too high a content deteriorates the toughness of the steel, the Cr content is controlled to be 0.20 to 0.30%.
Ni: ni can improve hardenability, corrosion resistance and guarantee toughness of steel at low temperature, but too high Ni content increases production cost, so that Ni content is controlled to be 0.15-0.30%.
Mo: the function of Mo in steel is mainly to improve hardenability, improve tempering resistance and prevent tempering brittleness. The addition of Mo favors the formation of bainite. Meanwhile, the overheating sensitivity and the graphitization tendency of the silicon steel are also reduced. The formation of white spots is reduced, and if the Mo content is too low, the above effect is limited, and if the Mo content is too high, the above effect is saturated, and the cost of the steel is increased. Therefore, the Mo content is controlled to be 0.30 to 0.40%.
P: micro segregation is formed when molten steel is solidified, and then the micro segregation is deviated to a grain boundary when the molten steel is heated at a temperature after austenite, so that the brittleness of steel is obviously increased, and the high-temperature tempering brittleness tendency of the steel is increased. Therefore, the P content should be controlled not to be higher than 0.015%.
S: the formation of MnS inclusions and segregation at grain boundaries deteriorate the toughness of the steel, thereby reducing the toughness and plasticity of the steel. Therefore, the S content should be controlled not to exceed 0.010%.
Al: besides reducing dissolved oxygen in the molten steel, aluminum can also play a role in refining grains. However, since the excessive Al content reduces harmful elements such as Ti in steel and is liable to cause contamination of molten steel by secondary oxidation during continuous casting, the Al content should be controlled to 0.015 to 0.040%.
The invention provides a production method of long-life drill rod steel, which comprises the following process flows of: electric arc furnace smelting → LF furnace refining → RH vacuum degassing → round billet continuous casting → heating of casting blank heating furnace → cogging → six-stand continuous rolling mill rolling to produce 150mmx150mm square billet.
Smelting in an electric arc furnace: in order to ensure the purity of the molten steel, the ladle smelted by the electric arc furnace requires bottom blowing argon in the whole process, the flow of the argon is adjusted, and the slag discharge amount in the tapping process is strictly controlled based on that the molten steel does not splash to the tapping ladle.
LF refining: in order to further improve the purity of molten steel, the slagging condition needs to be observed in time in the LF refining process, the white slag retention time is more than 20 minutes, and the final LF slag component requirement (TFe + MnO) is less than or equal to 0.8 percent.
RH vacuum degassing: the holding time is more than or equal to 20 minutes when the vacuum degree is less than or equal to 100Pa, and the [ H ] is less than or equal to 1.5ppm after vacuum treatment; in order to improve the purity of molten steel, ensure the weak stirring and soft blowing time before the molten steel is out of the station, observe the soft blowing effect, finely adjust the argon flow according to the soft blowing effect, and ensure that the liquid level of the molten steel is not exposed and the slag surface slightly fluctuates.
Continuous casting of round billets: in order to improve the purity of steel, protective casting is adopted in the whole continuous casting process, large ladle long nozzle argon blowing protection and medium ladle argon blowing protection are adopted for casting, superheat degree (15-30 ℃) of molten steel is strictly controlled in order to improve compactness of steel, three sections of electromagnetic stirring, M-EMS electromagnetic stirring, S-EMS electromagnetic stirring and F-EMS electromagnetic stirring are adopted for continuous casting, T.O content of steel billets is effectively guaranteed, alloy element segregation is controlled, local hardness of final drill rods is prevented from being higher or lower, and service life of the drill rods is prolonged.
Preferably, the M-EMS electromagnetic stirring current is 150-250A, and the frequency is 1.0-1.5 Hz; S-EMS electromagnetic stirring current is 250-350A, and the frequency is 10-15 Hz; the F-EMS electromagnetic stirring current is 350A-450A, and the frequency is 7-13 Hz.
Heating a casting blank heating furnace: for the requirements of the rolling process and for the solid dissolution of the carbonitrides in the austenite, the soaking zone temperature is set as: 1230-1260 ℃. Ensuring the full heating of the casting blank.
Cogging: the initial rolling temperature is controlled to be 1100-1140 ℃. The initial rolling temperature is too high, and the texture grains of the rolled material are coarse, which is not beneficial to texture refinement; the initial rolling temperature is too low, so that the final rolling temperature is too low, and the production is influenced.
Rolling by a six-stand continuous rolling mill: the finishing temperature is controlled to be 800-850 ℃. Is beneficial to further refining the final product structure. The final rolling temperature is too high, so that the effect of controlling rolling cannot be achieved; the final rolling temperature is too low, so that the rolling mill is difficult to bite, and even roll breakage and other accidents occur.
The invention adopts phi 600mm round billet continuous casting and small square billet (150mmx150mm) rolling, and the compression ratio is more than 12.
Compared with 55SiMnMo, the invention properly increases the content of C element in the aspect of component design, the high content of C is beneficial to the strength, hardness and the like of steel, the use environment of a drill rod is severe, the drill rod is generally used in mining, and the sufficient hardness of the drill rod needs to be ensured, (2) the content of Si in steel is reduced, because the over-high Si can increase the heat sensitivity and brittleness of materials, so that the fatigue life of the final drill rod is reduced, (3) a proper amount of Cr and Ni elements are added, Ni is non-carbide forming element and can exist in α phase or gamma phase in a mutual solution mode with Fe, so that the solid solution strengthening is realized, and the low-temperature toughness and fatigue resistance of the final drill rod are improved by refining α phase crystal grains.
Compared with the traditional continuous casting small square billet (150mmx150mm) production process, the invention adopts phi 600mm round billet continuous casting and small square billet (150mmx150mm) rolling, the compression ratio is more than 12, the large deformation promotes the recrystallization of the billet tissue in the rolling process, the condition of generating critical recrystallization is met, the permeability of deformation is obviously improved, and the deformation of the middle part of a rolled piece is obviously increased. Thereby achieving the purpose of controlling shrinkage cavity and loosening and prolonging the service life of the final drill rod.
Compared with the traditional M-EMS process only adopted in the small billet continuous casting process, the continuous casting method adopts three sections of electromagnetic stirring (M-EMS + S-EMS + F-EMS) and controls through proper electromagnetic stirring parameters, thereby effectively solving the problems of positive segregation peak of the casting billet 1/4 diameter and negative segregation in the adjacent area, preventing the local hardness of the final drill rod from being higher or lower, and prolonging the service life of the drill rod.
The key point of the invention is that the optimization adjustment of the components and the metallurgical quality control are organically combined, so that the high strength is obtained, and simultaneously, the excellent fatigue failure resistance and the lower cost are also obtained.
Compared with the prior art, the invention develops the high-strength high-toughness long-life drill rod steel by combining the two-fire-finished-material production process with the Cr, Ni and Mo composite alloying principle. The steel adopts a quenching and tempering (860 ℃ quenching +580 ℃ tempering) process, the metallographic structure is tempered martensite, the steel has good obdurability, the continuous casting process adopts three sections of electromagnetic stirring, the segregation of alloy elements of the steel is low, and no segregation of massive ferrite iron and martensite exists, so that the service life of the long-life drill rod steel produced by the method is prolonged by 30-40% compared with the service life of a drill rod made of continuous casting small square billets with the same specification.
Detailed Description
The following examples are intended to illustrate the invention, but the scope of protection of the invention is not limited to the following examples.
Example 1 to example 4
The production method of the long-life steel for the drill rod comprises the following steps:
electric arc furnace smelting → LF furnace refining → RH vacuum degassing → round billet continuous casting → heating of casting blank heating furnace → cogging mill rolling → six-stand continuous mill rolling. The method adopts phi 600mm round billet continuous casting and small square billet (150mmx150mm) rolling, and the compression ratio is more than 12. The steel for the long-life drill rod with the specification of 150mmx150mm is produced, the smelting chemical components of the steel in percentage by mass (wt%) are shown in table 1, and the specific production method comprises the following steps:
smelting in an electric arc furnace: in order to ensure the purity of the molten steel, the ladle smelted by the electric arc furnace requires bottom blowing argon in the whole process, the flow of the argon is adjusted, and the slag discharge amount in the tapping process is strictly controlled based on that the molten steel does not splash to the tapping ladle.
LF refining: in order to further improve the purity of molten steel, the slagging condition needs to be observed in time in the LF refining process, the white slag retention time is more than 20 minutes, and the final LF slag component requirement (TFe + MnO) is less than or equal to 0.8 percent. The specific parameters of the white slag retention time and the components in the production processes of examples 1 to 4 are shown in Table 2.
RH vacuum degassing: the holding time is more than or equal to 20 minutes when the vacuum degree is less than or equal to 100Pa, and the [ H ] is less than or equal to 1.5ppm after vacuum treatment; in order to improve the purity of molten steel, ensure the weak stirring and soft blowing time before the molten steel is out of the station, observe the soft blowing effect, finely adjust the argon flow according to the soft blowing effect, and ensure that the liquid level of the molten steel is not exposed and the slag surface slightly fluctuates. The vacuum degree and the holding time in the production process of examples 1 to 4 are shown in Table 2.
Continuous casting of round billets: in order to improve the purity of steel, protective casting is adopted in the whole continuous casting process, large ladle long nozzle argon blowing protection and medium ladle argon blowing protection are adopted for casting, superheat degree (15-30 ℃) of molten steel is strictly controlled in order to improve the compactness of steel, and three sections of electromagnetic stirring (M-EMS + S-EMS + F-EMS) are adopted for continuous casting, so that T.O content of steel billets is effectively guaranteed, alloy element segregation is controlled, partial high or low hardness of a final drill rod is prevented, and the service life of the drill rod is prolonged. Specific control parameters of the degree of superheat and three-stage electromagnetic stirring in the production processes of examples 1 to 4 are shown in Table 2.
Heating a casting blank heating furnace: for the requirements of the rolling process and for the solid dissolution of the carbonitrides in the austenite, the soaking zone temperature is set as: 1230-1260 ℃. Ensuring the full heating of the casting blank. Specific control parameters of the soaking section temperature in the production process of examples 1-4 are shown in Table 2.
Cogging: the initial rolling temperature is controlled to be 1100-1140 ℃. The initial rolling temperature is too high, and the texture grains of the rolled material are coarse, which is not beneficial to texture refinement; the initial rolling temperature is too low, so that the final rolling temperature is too low, and the production is influenced.
Rolling by a six-stand continuous rolling mill: the finishing temperature is controlled to be 800-850 ℃. Is beneficial to further refining the final product structure. The final rolling temperature is too high, so that the effect of controlling rolling cannot be achieved; the final rolling temperature is too low, so that the rolling mill is difficult to bite, and even roll breakage and other accidents occur. Specific control parameters of the finish rolling temperature in the production processes of examples 1 to 4 are shown in Table 2.
The steel production process parameters described in examples 1-4 are shown in table 2; the rest was performed according to the prior art. The mechanical performance indexes of the long-life drill rod made of the 150mmx150mm long-life drill rod steel produced in the examples 1 and 4 by heating → perforating → hot drawing → finished product → quenching and tempering (860 ℃ quenching +580 ℃ tempering) are shown in table 3; HRC hardness detection is carried out after a drill rod B22 multiplied by 2.5m is manufactured by a mechanical drilling method (GB/T230 metal Rockwell hardness test is adopted as a detection standard); the normal temperature hardness is shown in Table 4; the life test is carried out on the drill rod life test bed, and the life results are shown in Table 5.
Comparative examples 1 to 2
A production method of steel for a drill rod comprises the following process flows:
converter smelting → LF furnace refining → billet continuous casting. The steel for the drill rod with the specification of 150mmx150mm is produced, the smelting chemical components of the steel in percentage by weight (wt%) are shown in table 1, and the process parameters are shown in table 2; mechanical property indexes of the drill rod produced by adopting the 150mmx150mm continuous casting billet produced by the comparative example 1 and the comparative example 2 after heating → perforating → hot drawing → finished product → quenching and tempering (860 ℃ quenching +580 ℃ tempering) are shown in a table 3; HRC hardness detection is carried out after a drill rod B22 multiplied by 2.5m is manufactured by a mechanical drilling method (GB/T230 metal Rockwell hardness test is adopted as a detection standard); the normal temperature hardness of the drill rod is shown in Table 4; the life test is carried out on the drill rod life test bed, and the life results are shown in Table 5.
Table 1 mass percent (wt%) of the melting chemistry of each of the example and comparative steels, the balance being iron and unavoidable impurities.
| Examples | C | Si | Mn | P | S | Cr | Mo | Ni | Als |
| Example 1 | 0.64 | 0.51 | 0.81 | 0.010 | 0.003 | 0.25 | 0.35 | 0.24 | 0.024 |
| Example 2 | 0.65 | 0.50 | 0.82 | 0.010 | 0.002 | 0.26 | 0.34 | 0.23 | 0.020 |
| Example 3 | 0.63 | 0.52 | 0.80 | 0.009 | 0.001 | 0.24 | 0.35 | 0.21 | 0.027 |
| Example 4 | 0.62 | 0.49 | 0.79 | 0.008 | 0.002 | 0.27 | 0.33 | 0.22 | 0.031 |
| Comparative example 1 | 0.51 | 1.12 | 0.78 | 0.015 | 0.010 | - | 0.51 | - | 0.022 |
| Comparative example 2 | 0.59 | 1.30 | 0.63 | 0.017 | 0.012 | - | 0.42 | - | 0.025 |
TABLE 2 production Process parameters of steels for drill rods of examples and comparative examples
TABLE 2 Process parameters for electromagnetic stirring in the production of steel for drill rods of the examples and comparative examples
TABLE 3 mechanical Properties of drill rods of examples and comparative examples
TABLE 4 Normal temperature hardness of drill rods of examples and comparative examples
TABLE 5 Life of drill rods for each of the examples and comparative examples
| Examples | Life span |
| Example 1 | 25 minutes 45 seconds |
| Example 2 | 26 minutes and 12 seconds |
| Example 3 | 24 minutes 58 seconds |
| Example 4 | 27 minutes 19 seconds |
| Comparative example 1 | 18 minutes 43 seconds |
| Comparative example 2 | 19 minutes and 12 seconds |
The service life of the long-life drill rod steel produced by the invention is 30-40% longer than that of a rock drill rod made of continuous casting small square billets with the same specification.
Claims (10)
1. The steel for the long-life drill rod is characterized by comprising the following chemical components in percentage by mass: c: 0.60-0.70%, Si: 0.40-0.60%, Mn: 0.70-0.90%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent, Mo: 0.30-0.40%, Ni: 0.15-0.30%, Cr: 0.20-0.30%, Als: 0.015-0.040%, the rest is iron and inevitable impurities.
2. A method for producing the long life drill rod steel of claim 1, wherein the method comprises the following steps: electric arc furnace smelting → LF furnace refining → RH vacuum degassing → round billet continuous casting → heating of casting blank heating furnace → cogging → six-stand continuous rolling mill rolling.
3. The production method according to claim 2, characterized in that the LF refining: the white slag retention time is more than 20 minutes, and the final slag component of LF (ladle furnace) is required to be less than or equal to 0.8 percent (TFe + MnO).
4. The production method according to claim 2, characterized in that RH vacuum degassing: the holding time is more than or equal to 20 minutes when the vacuum degree is less than or equal to 100Pa, and the [ H ] is less than or equal to 1.5ppm after vacuum treatment.
5. The production method according to claim 2, wherein the degree of superheat of the molten steel is controlled to 15 to 30 ℃.
6. The production method according to claim 2, wherein the continuous casting employs three stages of electromagnetic stirring: M-EMS electromagnetic stirring, S-EMS electromagnetic stirring and F-EMS electromagnetic stirring.
7. The method as claimed in claim 6, wherein the M-EMS electromagnetic stirring current is 150-250A, the frequency is 1.0-1.5 Hz; S-EMS electromagnetic stirring current is 250-350A, and the frequency is 10-15 Hz; the F-EMS electromagnetic stirring current is 350A-450A, and the frequency is 7-13 Hz.
8. The production method according to claim 2, wherein the slab furnace heats: the temperature of the soaking section is set as follows: 1230-1260 ℃.
9. The production method according to claim 2, characterized in that the cogging: the initial rolling temperature is controlled to be 1100-1140 ℃.
10. The production method according to claim 2, wherein a six-stand continuous rolling mill rolls: the finishing temperature is controlled to be 800-850 ℃.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112322984A (en) * | 2020-11-16 | 2021-02-05 | 江苏联峰能源装备有限公司 | Steel for drill rod and preparation method thereof |
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| CN101542007A (en) * | 2006-09-01 | 2009-09-23 | 格奥尔格斯玛林许特有限公司 | Steel, and processing method for the production of higher-strength fracture-splittable machine components |
| CN101880822A (en) * | 2010-07-21 | 2010-11-10 | 武汉钢铁(集团)公司 | Hot rolled high-ductility carbon steel for passenger traffic steel rails |
| CN105568134A (en) * | 2016-01-05 | 2016-05-11 | 江阴兴澄特种钢铁有限公司 | Steel for carbon hub bearing of microalloying car and production method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57143465A (en) * | 1981-02-27 | 1982-09-04 | Sumitomo Metal Ind Ltd | Steel for railroad wheel with superior wear resistance and cracking loss resistance |
| JPH09235651A (en) * | 1996-02-28 | 1997-09-09 | Yanmar Diesel Engine Co Ltd | Wear resistant material and wear resistant machine parts |
| CN101542007A (en) * | 2006-09-01 | 2009-09-23 | 格奥尔格斯玛林许特有限公司 | Steel, and processing method for the production of higher-strength fracture-splittable machine components |
| CN101880822A (en) * | 2010-07-21 | 2010-11-10 | 武汉钢铁(集团)公司 | Hot rolled high-ductility carbon steel for passenger traffic steel rails |
| CN105568134A (en) * | 2016-01-05 | 2016-05-11 | 江阴兴澄特种钢铁有限公司 | Steel for carbon hub bearing of microalloying car and production method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN112322984A (en) * | 2020-11-16 | 2021-02-05 | 江苏联峰能源装备有限公司 | Steel for drill rod and preparation method thereof |
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