CN109402498B - High-temperature carburized gear steel and manufacturing method thereof - Google Patents
High-temperature carburized gear steel and manufacturing method thereof Download PDFInfo
- Publication number
- CN109402498B CN109402498B CN201810994814.XA CN201810994814A CN109402498B CN 109402498 B CN109402498 B CN 109402498B CN 201810994814 A CN201810994814 A CN 201810994814A CN 109402498 B CN109402498 B CN 109402498B
- Authority
- CN
- China
- Prior art keywords
- steel
- equal
- temperature
- percent
- less
- 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
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
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/28—Manufacture of steel in the converter
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
The invention relates to V, Ti composite microalloyed high-temperature carburized gear steel and a manufacturing method thereof, wherein the gear steel comprises the following chemical components in percentage by mass: c: 0.16-0.20%, Si: less than or equal to 0.08 percent, Mn: 0.90-1.10%, Cr: 1.25-1.40%, V: 0.02-0.04%, more than or equal to 0.015 and less than 0.020% of Ti, Al: 0.008-0.015%, N: 0.0080-0.0120%, P: less than or equal to 0.025 percent, S: 0.015 to 0.025%, O: less than or equal to 0.0013 percent, and the balance of Fe and inevitable impurities. Sufficient V (C, N) and Ti (C, N) precipitated phase pinning crystal boundaries are formed to inhibit grain growth, the austenite grain size is stabilized at 7.0-8.0 grade, the service fatigue life of the gear is prolonged, and the production cost is effectively reduced; and strictly controlling the Al content in the steel, controlling the Al content in a lower range and preventing a large amount of Al from being formed2O3The brittle inclusion blocks the water gap, ensures the stable and controllable quality and realizes the multi-furnace continuous casting production.
Description
Technical Field
The invention belongs to the technical field of special steel, and particularly relates to composite microalloyed steel for a high-temperature carburized automobile gear.
Background
In recent years, domestic high temperature carburization technology has begun to be applied in gear parts companies. A large number of researches show that when the carburizing temperature is increased to 950 ℃ from 920-930 ℃ in the prior art, the carburizing period can be reduced by about 30%, and when the carburizing temperature is increased to 1000 ℃, the carburizing period can be reduced by about 55%. However, when the carburizing temperature of the common gear steel reaches 950 ℃, a small amount of coarse austenite grains appear, which easily causes the gear deformation and greatly reduces the use performance of the gear; and when the carburizing temperature is 1000 ℃, a large amount of coarse austenite grains appear, so that the gear parts are scrapped.
Conventionally, in order to prevent austenite grains from being abnormally coarse after high-temperature carburization of gears, a small amount of Nb or Ti alloy is mainly added to pin grain boundaries by forming Nb (C, N) and Ti (C, N) particles, thereby suppressing austenite grain growth. Patent CN103361559A discloses a Nb and Ti composite micro-alloying high temperature carburized gear steel. By adding 0.02-0.06% of Ti, 0.02-0.06% of Nb and 0.015-0.035% of Al, Ti (C, N) and Nb (C, N) precipitation phase pinning grain boundaries are formed, and the austenite grain size of the steel can be maintained above 8.0 grade after the steel is kept at 1000 ℃ for 1 hour and 6 hours, and no mixed crystal phenomenon is found. However, addition of a large amount of Nb easily causes cracking of a cast slab and greatly increases production cost, and thus it is difficult to realize industrial production.
In order to prevent the coarsening of the high-temperature carburized austenite grains of the gear, a large amount of Al and N alloy is added, the Al/N ratio is controlled within a proper range, and the growth of the austenite grains is inhibited by forming a large amount of AlN precipitated phases. Patent CN102560255A discloses a steel for high temperature vacuum carburized gears. By adding 0.033-0.055% of Al and 0.016-0.030% of N and controlling the Al/N ratio within the range of 0.60-1.80, the grain of the gear steel is kept at 7.0-8.0 grade after vacuum carburization for 4 hours at 1000 ℃. However, in the continuous casting of molten steel, a large amount of Al is formed by adding a large amount of Al2O3And the water gap of the continuous casting tundish, which is easily blocked, cannot be removed, so that the pouring is difficult, and the continuous production cannot be realized. At the same time, too much Al is present in the steel2O3The inclusion reduces the fatigue performance of the gear.
Disclosure of Invention
In order to solve the problems, the invention provides high-temperature carburized gear steel and a manufacturing method thereof, which achieve the purposes of reducing the production cost and realizing continuous casting production by combining reasonable component control with corresponding smelting procedures.
In order to achieve the purpose, the technical scheme of the invention is as follows:
the high-temperature carburized gear steel comprises the following chemical components in percentage by mass: c: 0.16-0.20%, Si: less than or equal to 0.08 percent, Mn: 0.90-1.10%, Cr: 1.25-1.40%, V: 0.02-0.04%, more than or equal to 0.015 and less than 0.020% of Ti, Al: 0.008-0.015%, N: 0.0080-0.0120%, P: less than or equal to 0.025 percent, S: 0.015 to 0.025%, O: less than or equal to 0.0013 percent, and the balance of Fe and inevitable impurities.
In the steel composition design, in order to solve the cost problem, a small amount of V microalloy elements are added into the steel, the addition of Nb is cancelled, the Ti content is reduced, and the production cost is effectively reduced.
The preparation method of the high-temperature carburized gear steel comprises the following steps:
the first step is as follows: smelting in a converter, adding about 20 percent of scrap steel into the converter, then adding molten iron for smelting, and tapping at the end point to control the target: c is more than or equal to 0.08 percent, P is less than or equal to 0.015 percent, and the sliding plate slag stopping operation is carried out in the tapping process to reduce the slag; alloying is started about 90 seconds after tapping is started, and the adding sequence is as follows: aluminum iron, carbon powder, alloy and lime, wherein the adding amount of the aluminum iron alloy is controlled to be 80 +/-20 kg; ensuring the tapping temperature to be more than or equal to 1610 ℃;
the second step is that: refining in an LF ladle furnace, controlling the alkalinity of furnace slag to be 2.0-3.0, and simultaneously controlling the flow of Ar gas well to prevent slag entrapment caused by severe rolling of molten steel; comprehensive deoxidation is carried out by adopting a slag surface composite deoxidizer and silicon carbide diffusion deoxidation, the using amount of the slag surface composite deoxidizer is more than or equal to 150kg, and more than or equal to 80kg of silicon carbide and a small amount of ferrosilicon powder are added in the middle and later stages of smelting to maintain the slag;
the third step: RH vacuum degassing, namely adding ferrotitanium for nitrogen fixation after vacuum treatment is carried out on the molten steel for 5min, and keeping the vacuum degree below 0.266kPa for more than or equal to 18min, thereby being beneficial to reducing large-particle inclusions; in order to ensure that nitrogen is stable and controllable, nitrogen is increased by blowing nitrogen in the whole process in vacuum treatment, and nitrogen is increased by feeding a nitrogen-chromium line after the vacuum treatment is finished; after the vacuum treatment is finished, the calcium treatment is forbidden to prevent the formation of Ca and Al composite inclusions from blocking a water gap; after vacuum treatment, hoisting the steel ladle to a soft argon blowing station for soft argon blowing operation, keeping argon blowing for more than 20min to promote floating, gathering and removing of impurities, and strictly keeping molten steel bare on the premise that the slag surface is not blown broken and slightly fluctuated by the soft argon blowing flow;
the fourth step: and in the continuous casting process, the whole-process protective pouring is carried out on the molten steel by using measures such as argon sealing of a large ladle long nozzle, immersion of a middle ladle nozzle, covering agent of a middle ladle, mold protecting slag and the like, the pouring temperature of the middle ladle is controlled at 1533 +/-10 ℃, the pouring is carried out at a constant pulling speed, and meanwhile, the internal quality of a casting blank is improved by using process measures such as electromagnetic stirring of a crystallizer, weak cooling of secondary cooling water and the like. In order to prevent the casting blank from generating micro cracks, the casting blank is hung into a slow cooling pit for high-temperature slow cooling after being cut, and the surface temperature of the cast blank in the pit is ensured to be more than or equal to 610 ℃.
The fifth step: heating and rolling a casting blank into round steel, taking a round steel sample to simulate a carburizing and quenching process, wherein the process comprises the following steps: carburizing at 1010, 1020 ℃ and 1030 ℃ for 2 hours, 4 hours and 6 hours, quenching at 860 ℃ and tempering at 200 ℃.
In the design of the manufacturing method, the stopper curve in the continuous casting process is strictly controlled in the continuous casting process, and the steady-state control of the stopper curve in the casting process is kept.
The invention has the beneficial effects that: by adopting V, Ti composite microalloying design, in the component design, enough V (C, N) and Ti (C, N) precipitated phase pinning crystal boundaries are ensured to be formed to inhibit the growth of crystal grains, and the production cost is effectively reduced.
In order to reduce the degree of internal oxidation of grain boundaries during high-temperature carburization of gears, the Si content in steel is designed to be controlled within a lower range.
And by designing low Al content (0.008-0.015%), and combining effective control of smelting low oxygen content, Al is reduced2O3Amount of brittle inclusion formation; the method has the advantages that the calcium treatment is strictly forbidden after vacuum treatment, the soft argon blowing time is prolonged to promote the floating removal of large-size impurities, the enrichment of the impurities on the inner side of a water gap is greatly reduced, the steady-state control of a stopper rod curve in the casting process is realized, the stopper rod curve is prevented from being involved in the large-size impurities due to sudden fluctuation, at least 6-furnace continuous casting production can be realized, and the service fatigue life of the gear is obviously prolonged;
casting blanks are put into a pit at high temperature for slow cooling, so that microcracks are prevented from being generated on the casting blanks and the round steel, the ultrasonic flaw detection qualified rate of the rolled round steel is ensured to reach more than 99.5%, and the quality qualified rate of products is improved. By adopting the components and the process design, the high-temperature carburizing process of a gear processing enterprise is simulated, the heat is preserved for 2-6 hours at the temperature of 1000-1030 ℃ according to the carburizing and quenching process in a laboratory, the austenite grain size is kept at 7.5-8.0 grade, and the mixed crystal phenomenon is avoided; the gear steel product can promote the carburization of gear processing enterprises at the temperature of more than 1000 ℃, the austenite grain size is kept at 7.5-8.0 grade, the mixed crystal phenomenon is avoided, the carburization period can be greatly shortened, the production efficiency is improved, and the production cost is reduced.
Detailed Description
The melting chemical compositions (wt%) of the manufactured examples 1, 2 and 3 are shown in table 1, using the chemical composition ranges according to the present invention; converter smelting, LF refining, RH refining and square billet continuous casting are adopted, a plurality of smelted furnace billets are heated and rolled into round steel with the specification of 30-60 mm, the round steel is cooled to room temperature in a natural cooling mode after rolling, and the manufacturing process conditions are shown in table 2. The method comprises the steps of carrying out off-line chamfering and straightening on the round steel, carrying out ultrasonic flaw detection according to the grade A of the national standard GB/T4162, sampling and detecting the tissue condition of the round steel, wherein the ultrasonic flaw detection and the round steel detection results are shown in the table 3, and large-size fragile B-type inclusions with the width larger than 15um are not detected. A simulated carburizing and quenching test is carried out on rolled round steel, and the simulated carburizing and quenching process comprises the following steps: carburizing at 1010 deg.C, 1020 deg.C and 1030 deg.C for 2 hr, 4 hr and 6 hr, quenching at 860 deg.C, and tempering at 200 deg.C. The austenitic grain size was then evaluated according to the standard GB/T6394, the results of which are shown in Table 4.
TABLE 1V, Ti microalloyed gear steel chemistry (Wt,%)
TABLE 2 smelting and continuous casting Process conditions
TABLE 3 structural condition of Gear Steel
TABLE 4 simulated high temperature carburized Gear Steel Austenite grain size
The gear steel produced by the method has stable and controllable continuous casting process, the stopper rod curve is stably controlled, the continuous 6-furnace casting production can be realized, micro cracks do not appear on the casting blank and the rolled round steel, and the ultrasonic flaw detection qualification rate of the round steel is very high; the control of non-metallic inclusions is good, particularly, the level of brittle B-type and D-type inclusions is low, and B-type inclusions with the width larger than 15um do not exist, so that the service fatigue life of the gear is prolonged. The adoption of low V, Ti microalloying can still ensure that the high-temperature carburization austenite grains with the temperature of 1000-1030 ℃ for 2-6 h do not grow, and can effectively realize low-cost mass production; meanwhile, the novel gear steel is applied to gear processing enterprises, the gear carburizing period can be effectively shortened under the condition of higher carburizing temperature, and the production cost is reduced.
Claims (4)
1. The high-temperature carburized gear steel is characterized by comprising the following components in percentage by weight:
c: 0.16-0.20%, Si: less than or equal to 0.08 percent, Mn: 0.90-1.10%, Cr: 1.25-1.40%, V: 0.02-0.04%, more than or equal to 0.015 and less than 0.020% of Ti, Al: 0.008-0.015%, N: 0.0080-0.0120%, P: less than or equal to 0.025 percent, S: 0.015 to 0.025%, O: less than or equal to 0.0013 percent, and the balance of Fe and inevitable impurities; the manufacturing method of the high-temperature carburized gear steel comprises the following steps:
(1) smelting in a converter: adding 20% of scrap steel into the converter, carrying out sliding plate slag blocking operation in the tapping process to reduce slag, alloying after 90 seconds, and adding 80 plus or minus 20kg of aluminum-iron alloy for pre-deoxidation;
(2) refining in an LF ladle furnace: controlling the alkalinity of the slag to be 2.0-3.0, and simultaneously controlling the flow of Ar gas well to prevent slag entrapment caused by severe rolling of molten steel; comprehensive deoxidation is carried out by adopting a slag surface composite deoxidizer and silicon carbide diffusion deoxidation, the dosage of the slag surface composite deoxidizer is more than or equal to 150kg, and the addition of silicon carbide in the middle and later stages of smelting is more than or equal to 80 kg;
(3) RH vacuum degassing: after vacuum treatment of molten steel for 5min, adding ferrotitanium to fix nitrogen, and keeping the vacuum degree below 0.266kPa for more than or equal to 18 min; nitrogen is blown in the whole process to increase the nitrogen, and nitrogen is increased by feeding a nitrogen chromium line after the vacuum treatment is finished; after the treatment is finished, the calcium treatment is forbidden; soft argon blowing is carried out for more than 20min, so that floating, gathering and removing of impurities are promoted;
(4) continuous casting: in the continuous casting process, the whole-process protective pouring is carried out on the molten steel by using measures of argon sealing of a large ladle long nozzle, immersing of a middle ladle nozzle, covering of a middle ladle covering agent and mold powder, the pouring temperature of a middle ladle is controlled at 1533 +/-10 ℃, the pouring is carried out at a constant pulling speed, and the internal quality of a casting blank is improved by using process measures of electromagnetic stirring of a mold and weak cooling of secondary cooling water; in order to prevent the casting blank from generating microcracks, the casting blank is hoisted into a slow cooling pit for high-temperature slow cooling after being cut, and the surface temperature of the pit is ensured to be more than or equal to 610 ℃;
(5) high-temperature carburizing heat treatment: heating and rolling the continuous casting billet into round steel with different specifications, taking the round steel to simulate high-temperature carburization, wherein the carburization temperature is 1000-1030 ℃, the heat preservation time is 2-6 h, the grain size grade of the high-temperature carburization is 7.0-8.0, and the phenomenon of mixed crystals is avoided.
2. A high temperature carburized gear steel in accordance with claim 1 further characterized by: and V: 0.026-0.031%, Ti: 0.017 to 0.018 percent.
3. A high temperature carburized gear steel according to claim 1 or 2 characterized in that: in order to control the quantity and grade of B-type inclusions and large-particle inclusions in steel, Al/N is controlled to be 1.0-1.8.
4. A high temperature carburized gear steel as recited in claim 1 in which: and (4) strictly controlling the stopper curve in the continuous casting process in the step (4) and keeping the stable control of the stopper curve in the casting process.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810994814.XA CN109402498B (en) | 2018-08-29 | 2018-08-29 | High-temperature carburized gear steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810994814.XA CN109402498B (en) | 2018-08-29 | 2018-08-29 | High-temperature carburized gear steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109402498A CN109402498A (en) | 2019-03-01 |
| CN109402498B true CN109402498B (en) | 2020-08-28 |
Family
ID=65463737
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810994814.XA Active CN109402498B (en) | 2018-08-29 | 2018-08-29 | High-temperature carburized gear steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109402498B (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110172638B (en) * | 2019-05-10 | 2021-06-15 | 武汉钢铁有限公司 | High-temperature carburized gear steel and production method thereof |
| CN110373607B (en) * | 2019-07-25 | 2021-04-02 | 广东韶钢松山股份有限公司 | High-temperature carburized steel, high-temperature carburized steel component and preparation method thereof |
| CN111766257A (en) * | 2020-07-08 | 2020-10-13 | 宝钢特钢韶关有限公司 | Steel austenite grain boundary display method and steel austenite grain size evaluation method |
| CN112593036A (en) * | 2020-11-30 | 2021-04-02 | 江苏联峰能源装备有限公司 | Low-silicon microalloyed high-temperature carburized gear steel and manufacturing method thereof |
| CN115261715A (en) * | 2021-04-29 | 2022-11-01 | 宝山钢铁股份有限公司 | High-temperature carburized gear shaft steel and manufacturing method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101960035A (en) * | 2009-01-16 | 2011-01-26 | 新日本制铁株式会社 | Steel for high-frequency hardening |
| CN102282282A (en) * | 2009-01-16 | 2011-12-14 | 新日本制铁株式会社 | Steel for surface hardening for machine structural use, and component for machine structural use |
| CN102317490A (en) * | 2009-03-30 | 2012-01-11 | 新日本制铁株式会社 | Carburized steel part |
| CN102459678A (en) * | 2009-05-27 | 2012-05-16 | 住友金属工业株式会社 | Carburized component and manufacturing method therefor |
| CN102471842A (en) * | 2010-03-10 | 2012-05-23 | 新日本制铁株式会社 | Carburized steel component excellent in low-cycle bending fatigue strength |
| CN102560255A (en) * | 2012-01-31 | 2012-07-11 | 宝山钢铁股份有限公司 | High-temperature vacuum carburized gear steel |
| CN103589957A (en) * | 2013-11-28 | 2014-02-19 | 广东韶钢松山股份有限公司 | CrMnTi series gear steel production method |
-
2018
- 2018-08-29 CN CN201810994814.XA patent/CN109402498B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101960035A (en) * | 2009-01-16 | 2011-01-26 | 新日本制铁株式会社 | Steel for high-frequency hardening |
| CN102282282A (en) * | 2009-01-16 | 2011-12-14 | 新日本制铁株式会社 | Steel for surface hardening for machine structural use, and component for machine structural use |
| CN102317490A (en) * | 2009-03-30 | 2012-01-11 | 新日本制铁株式会社 | Carburized steel part |
| CN102459678A (en) * | 2009-05-27 | 2012-05-16 | 住友金属工业株式会社 | Carburized component and manufacturing method therefor |
| CN102471842A (en) * | 2010-03-10 | 2012-05-23 | 新日本制铁株式会社 | Carburized steel component excellent in low-cycle bending fatigue strength |
| CN103382538A (en) * | 2010-03-10 | 2013-11-06 | 新日铁住金株式会社 | Carburized steel component excellent in low-cycle bending fatigue strength |
| CN102560255A (en) * | 2012-01-31 | 2012-07-11 | 宝山钢铁股份有限公司 | High-temperature vacuum carburized gear steel |
| CN103589957A (en) * | 2013-11-28 | 2014-02-19 | 广东韶钢松山股份有限公司 | CrMnTi series gear steel production method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109402498A (en) | 2019-03-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109402498B (en) | High-temperature carburized gear steel and manufacturing method thereof | |
| CN108660381B (en) | A kind of low-cost manufacture method for protecting Q345B grades of steel plates of flaw detection | |
| CN110373607B (en) | High-temperature carburized steel, high-temperature carburized steel component and preparation method thereof | |
| CN108866444B (en) | Corrosion-resistant mirror surface die steel and preparation method thereof | |
| CN109852893B (en) | Low-temperature high-toughness refractory steel and preparation method thereof | |
| CN109161632B (en) | Production method for controlling large-size hard inclusions in spring steel wire rod | |
| CN114134430B (en) | High-hardenability 35SiMnCrMoB steel for wear-resistant parts of engineering machinery and manufacturing method thereof | |
| CN110184548B (en) | Method for refining solidification structure of high manganese steel continuous casting billet | |
| CN110408834B (en) | Method for improving flaw detection qualification rate of steel ingot low-Si hydro Cr-Mo steel | |
| CN112359279B (en) | Alloy structure steel wire rod for shaft and preparation method thereof | |
| CN108893682B (en) | Die steel billet and preparation method thereof | |
| CN104233098A (en) | Low-cost 60Si2Mn spring steel and production technology thereof | |
| JP2024515134A (en) | Steel for high temperature carburizing gear shaft and manufacturing method of the steel | |
| CN104818426A (en) | High-strength microalloyed rare-earth cast steel and preparation method thereof | |
| WO2018018389A1 (en) | High-strength microalloyed rare-earth cast steel | |
| WO2019169548A1 (en) | Low-strength cast steel micro-alloyed with rare earth | |
| CN113528976B (en) | Non-quenched and tempered bar without surface cracks and preparation method thereof | |
| CN109868415B (en) | Smelting method of low-sulfur low-boron pipeline steel | |
| CN114395727A (en) | Smelting and continuous casting process of martensite precipitation hardening stainless steel | |
| JP5708349B2 (en) | Steel with excellent weld heat affected zone toughness | |
| CN109487155A (en) | High-voltage oil cylinder hydraulic stem non-hardened and tempered steel and its production method | |
| WO2019169549A1 (en) | Cast steel micro-alloyed with rare earth | |
| CN109778073B (en) | Free-cutting steel for automobile synchronizer and preparation method thereof | |
| CN109234632B (en) | Easy-to-weld corrosion-resistant high-strength Q690E steel plate for deep sea submarine with thickness of 80-120mm and production method thereof | |
| CN112593036A (en) | Low-silicon microalloyed high-temperature carburized gear steel and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| CP01 | Change in the name or title of a patent holder |
Address after: 512123 special bar plant, MABA Town, Qujiang District, Shaoguan City, Guangdong Province Patentee after: Baowu jiefuyi Special Steel Co.,Ltd. Address before: 512123 special bar plant, MABA Town, Qujiang District, Shaoguan City, Guangdong Province Patentee before: BAOSTEEL SPECIAL STEEL SHAOGUAN Co.,Ltd. |
|
| CP01 | Change in the name or title of a patent holder |