CN101397636A - High toughness ring chain steel for mine and method for producing the same - Google Patents
High toughness ring chain steel for mine and method for producing the same Download PDFInfo
- Publication number
- CN101397636A CN101397636A CNA2007100463959A CN200710046395A CN101397636A CN 101397636 A CN101397636 A CN 101397636A CN A2007100463959 A CNA2007100463959 A CN A2007100463959A CN 200710046395 A CN200710046395 A CN 200710046395A CN 101397636 A CN101397636 A CN 101397636A
- Authority
- CN
- China
- Prior art keywords
- steel
- percent
- ring chain
- temperature
- temperatures
- 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.)
- Granted
Links
Images
Abstract
The invention discloses a high strength and toughness steel used for a ring chain, wherein, the chemical elementary compositions based on weight percentage are as follows: C: 0.20 to 0.26 percent, Mn: 1.10 to 1.40 percent, Ni: 0.85 to 1.15 percent, Cr: 0.40 to 0.60 percent, Mo: 0.40 to 0.60 percent, V: 0.03 to 0.10 percent, Al: 0.020 to 0.050 percent, Si: less than or equal to 0.25 percent, Cu: less than or equal to 0.25 percent, S: less than or equal to 0.020 percent, P: less than or equal to 0.020percent, and Fe and inevitable impurity as the rest. According to general arc melting, refining technology and given alloy elements ratio, the invention uses continuous casting techniques to produce casting billets. The average casting temperature is 1150 to 1200 DEG C, beginning temperature of rolling is 1130 to 1180 DEG C, and final temperature of rolling is 760 to 800 DEG C; after being rolled, the billets are cooled in water and air; Then the hot rolled steel bars are annealed at 680 to 710 DEG C for 8 to 12 hours, and the tapping temperature is less than or equal to 250 DEG C, and then cooled in air, and wind is avoided. Therefore, the high strength and toughness ring chain steel forms into spherical pearlite, and has high cleanliness, uniform and fine structure, uniform and moderate hardness and excellent comprehensive mechanical properties after heat treatment.
Description
Technical field
The present invention relates to the composition design and the manufacture method thereof of metallurgy industry structure iron, refer in particular to the composition design and the manufacture method thereof of high strength, high tenacity mine ring chain steel.
Background technology
Coal is the major portion of China's Energy Mix, and wherein down-hole coal excavation occupies very big proportion again in coal in China is produced.As the transmission chain-round-link chain on scraper conveyer and the various plough is the key component and the consumable accessory of these equipment.Press national Specification, round-link chain is divided into B, three ranks of C and D.B level round-link chain is mainly used in less, the not too important occasion of load, and its starting material adopt low-carbon alloy steel usually, as: 20MnSi and 23MnSiV.D level round-link chain requires that very high intensity is arranged, and (tensile strength Rm 〉=1470Mpa), the counter stress corrosion is strict, so fail mass production all the time.C level round-link chain is that the present usage quantity of China is bigger, and industrial application is a class round-link chain more widely, and its specification is ∮ 4mm-∮ 45mm, wherein≤the employing 25MnV steel of ∮ 18mm, the 23MnNiMoCr54 steel of the employing import of 〉=∮ 22mm.Domestic have tens tame special steel factories on the basis of chemical ingredients, microstructure and the mechanical property of the 23MnNiMoCr54 steel of having analyzed Japan and German import, the 23MnNiMoCr54 steel is produced in imitation, but all do not have successfully, tissue odds is even, the obdurability coupling is undesirable, cause the long-term dependence on import of many chain manufacturers, need expend a large amount of foreign exchanges every year by this steel of external import.The 23MnNiMoCr54 steel is the moral target trade mark, its main component is: carbon: 0.20～0.26%, and manganese: 1.10～1.40%, nickel: 0.90～1.10%, chromium: 0.40～0.60%, molybdenum: 0.50～0.60%, Al:0.020～0.050%, silicon :≤0.25%, copper≤0.25%, sulphur≤0.025%, phosphorus≤0.025%, surplus is Fe.This steel grade does not contain " vanadium ".Its manufacturing process is external restricted data, does not mention in the literature.The main deficiency of materials overseas is costing an arm and a leg of it, is 2～3 times of home made materials.
In recent years, the application for a patent for invention of round-link chain steel is existing a lot, as: the application for a patent for invention CN85103476 of D level ring chain steel, form and see Table 1, though its intensity can reach requirement, the obdurability coupling is undesirable, can't guarantee stress corrosion resistant under the environment for use of D level round-link chain; Application number is that 200610013245.3,200610072702.6 and 200610048121.9 application for a patent for invention discloses C level ring chain steel, forms to see Table 1.Though not add Ni or/and Cr unit usually reduce cost, but on the inner quality of steel, can't reach the hardening capacity of high request, the obdurability coupling is undesirable, actual can only being limited in below the φ 26mm on the production specification, particularly also contain easy oxidation elements Si, cause the seam organization of round-link chain undesirable etc. easily.
Above-mentioned existing invention steel, C level ring chain steel particularly, still it is a lot of to go wrong in the production use, in case form when supplying in batches, in use, be mainly reflected in the deficiency of the following aspects: at first, be organized as perlite+ferrite in the inner quality of homemade steel, do not reach spherulitic, ferrite is on the high side, hardness is at HRW180-250, deviation is bigger, and homogeneity is undesirable, and original structure and import steel have very big difference, carbide particle is thick, and size is extremely inhomogeneous; Secondly, the round-link chain that the 23MnNiCrMo54 steel of domestic steel mill reference inlet port material component production is made, because factors such as production unit and rolling technological parameter, the coupling of obdurability is undesirable, all do not reach the GB requirement fatigue lifetime, the round-link chain poor-performing that is compiled into, stability is low, cause the amount of doing over again to increase energy dissipation; The 3rd, homemade steel after heat treatment, tissue odds is even, the commissure is organized thick, has bigger overheated tendency, this also is to cause one of weldability and the underproof major reason of fatigue property; The 4th, still there is blank in domestic the use in circular chain steel production on the specification, according to statistics, China applies for the maximum in actual use specification that can only reach ∮ 26mm of the ring chain steel of patent of invention at present, and on the ring chain steel of 〉=∮ 30mm specification, or based on import, the production domesticization of still being unrealized.
Table 1 ring chain steel patent application in recent years situation
| Patent application | C wt％ | Si wt％ | Mn wt％ | Ni wt％ | Cr wt％ | Mo wt％ | Al wt％ | Other elements wt% |
| CN85103476 (D level) | 0.21～ 0.27 | 0.65～ 0.95 | 1.10～ 1.40 | 0.80～ 1.10 | ≤0.35 | 0.10～ 0.20 | 0.020～ 0.050 | P、S≤0.035 Cu≤0.25 |
| (200610013245.3 C level) | 0.17～ 0.30 | 0.10～ 0.80 | 1.20～ 2.00 | — | 0.10～ 0.80 | 0.10～ 0.50 | 0.020～ 0.050 | P, S≤0.030 Cu≤0.20 V and/or Nb0.03～0.15 |
| (200610072702.6 C level) | 0.17～ 0.30 | 0.10～ 0.80 | 1.00～ 2.00 | — | — | 0.10～ 0.50 | — | V0.02～0.15 |
| (200610048121.9 C level) | 0.18～ 0.30 | 0.20～ 0.80 | 1.20～ 2.00 | — | — | 0.15～ 0.50 | 0.020～ 0.050 | P、S≤0.030 Cu≤0.20 Nb0.02～0.06 |
Summary of the invention
The technical problem to be solved in the present invention provides a kind of C grade circle chain of mine steel, and the ring chain steel for mine tissue odds that solves prior art is even, and intensity, plasticity is on the low side and it is bad to mould coupling by force, is prone to the problem of defective grade fatigue lifetime.Careful by adopting the microalloying continuously cast bloom to mass-produce homogeneous microstructure, improve comprehensive mechanical performance, improve fatigue lifetime, improve the C level ring chain steel of whole piece round-link chain resistance to overturning, make its each technical indicator all can be suitable with moral target 23MnNiMoCr54 steel, further satisfy the development of mining machinery, satisfy the demand of the C level ring chain steel of the above specification of domestic ∮ 30mm.
High-strong toughness ring chain steel of the present invention, its chemical element composition by weight percentage is: carbon: 0.20～0.26%, manganese: 1.10～1.40%, nickel: 0.85～1.15%, chromium: 0.40～0.60%, molybdenum: 0.40～0.60%, vanadium: 0.03～0.10%, Al:0.020～0.050%, silicon :≤0.25%, copper≤0.25%, sulphur≤0.020%, phosphorus≤0.020%, surplus is Fe and unavoidable impurities.
Composition design reason of the present invention or principle are as follows:
Carbon: be the principal element that improves big specification C level ring chain steel intensity, guarantee the necessary certain carbon content of certain intensity, but carbon is unfavorable to plasticity, particularly when Mn content is higher, carbon content is unfavorable for welding property greater than 0.30%, in order to ensure the coupling of C and Mn content, so it is comparatively reasonable to control 0.20～0.26% carbon content.
Manganese: manganese is one of main alloy element of adding in the steel of the present invention, and it is non-carbide forming element, can strengthen austenitic stability, reduces the Ms point, and that plays solution strengthening in steel is used for improving intensity, improves the hardening capacity of steel; Because the C level ring chain steel of national Specification should have phosphorus, low-sulfur content feature, and the avidity of manganese and oxygen is stronger, when steel-making, can play desoxydatoin, help later desulfurization process.But manganese element is too much, can cause grain growth, increases the fragility of steel, can bring into play good effect so the manganese content in the ring chain steel is controlled at 1.10～1.40% in steel of the present invention.
Nickel: nickel is one of main alloy element of adding in the steel of the present invention, the adding of nickel element not only can improve the toughness of steel, can also improve the hardening capacity of steel, but Ni is again valuable alloying element, the too much affiliation that adds improves manufacturing cost, so the nickel of this invention steel is controlled at 0.85～1.15%, especially to be advisable 0.90～1.10%.
Chromium: chromium is one of main alloy element of adding in the steel of the present invention, and it is a carbide forming element, stablizes the formation of the carbide of chromium, and the effect of the welding joint place heat affected zone grain growth that slows down is arranged, and is very favorable for the weld structure of round-link chain; Simultaneously, nickel and chromium element can increase austenitic cold energy power excessively, thus thinning microstructure, the effect that is strengthened, nickel and chromium can be brought into play certain corrosion resistance nature again, help round-link chain and use under moist environment.So being controlled at 0.40～0.60%, chromium content just can play above-mentioned beneficial effect.
Molybdenum: molybdenum is one of main alloy element of adding in the steel of the present invention, and molybdenum has the obvious suppression effect to perlitic transformation, and very little to the retardation function of bainite transformation, helps obtaining under the air cooling condition bainite structure; Molybdenum as in the strong carbide forming element can hinder consumingly carbide forming core and grow up, simultaneously can also effectively improve hardening capacity, for ring chain steel, the adding of molybdenum can also improve the flash welding performance of steel, particularly improve the anti-overheated ability in the butt welding process, simultaneously, the combined action of molybdenum and manganese, can significantly improve austenitic stability again, improve the hardening capacity of steel, for guaranteeing the mechanical property of big specification (〉=∮ 30mm) round-link chain, the molybdenum of steel adding 0.40～0.60% of the present invention is most economical effective content.
Vanadium: vanadium adds as micro alloying element in this invention steel, V can add in the molten steel easily, because vanadium can form vanadium carbide or vanadium nitride with general carbon that all contains in the steel and nitrogen element, and having the crystalline structure and the lattice constant of identical sodium-chlor type, vanadium carbide or vanadium nitride be more or less the same, thereby will dissolve each other fully usually and form the carbon vanadium nitride, and the solubleness of vanadium in heat-processed is very big, comes crystal grain thinning by its precipitation of carbonitride, tissue and improve intensity.Carbide and nitride particles are tiny more, and the precipitation strength effect is obvious more.So add 0.03～0.10% vanadium of trace in steel of the present invention, for the tissue of refinement ring chain steel, the coupling and the fatigue property that improve its obdurability are very effective.
Aluminium: belong to the crystal grain thinning element.Aluminium element cooperates further crystal grain thinning with above-mentioned element, and improves the toughness of steel.Easily increasing the chance that steel inclusion produces but experience shows too much aluminium, is that the assurance round-link chain can stably be resisted the strain fragility in the use simultaneously, should comprise 0.020～0.050% aluminium in this invention steel.
Its content should be low as far as possible under the situation of technical qualification and manufacturing processed permission for copper, phosphorus, sulphur simultaneously, to reduce the poly-partially of original austenite crystal prevention place, improves toughness.Residual element and gas content are controlled at suitable low levels level, make steel have quite high purity, element silicon particularly, silicon is easy to oxidation in steel, form inclusion, to cause serious harm to the weld seam of round-link chain, silicon will increase the resistance of material simultaneously, when carrying out flash welding, will make the flame current of material increase, produce high temperature, cause the overheated of material.So in this invention steel, do not add.
The manufacture method of high-strong toughness of the present invention mine ring chain steel is characterized in that: arc melting routinely, refinery practice and given alloying element ratio, adopt continuous casting process to produce strand; The continuous-cast blank soaking temperature: 1150～1200 ℃, 1130～1180 ℃ of start rolling temperatures, 760～800 ℃ of finishing temperatures; Wear water cooling after rolling, again air cooling; Rolled steel bar need be annealed, 680～710 ℃ of annealing temperatures, 8～12 hours hold-times, tapping temperature≤250 ℃, air cooling, wind sheltering.
More specifically, the preparation method of high-strong toughness ring chain steel, adopt the three-steps process flow process: the first step: electric arc furnace just refines → ladle furnace vacuum refinement → continuous casting; Second step: rolling mill hot-work is rolled into rod iron; The 3rd step: rod iron annealing.
Wherein, the first step, electric arc furnace smelting-ladle refining-continuous casting
Carrying out molten steel in 60～200 tons electric arc furnace just refines; The ladle refining of corresponding tonnage; Continuous casting; Produce 140 * 140mm
2～450 * 450mm
2The qualified continuously cast bloom of cross dimensions:
(1) molten steel just refines: furnace charge is selected low P, S steel scrap, crop and high duty pig iron for use; Alloy need be prepared ferrochrome, low-phosphorous ferromanganese, molybdenum-iron, nickel ball etc.; Reductive agent: calcium carbide, carbon dust, aluminium powder; Oxidation period: diligent stream slag removes P; Tapping condition: T1630～1650 ℃; [P]≤0.010%, [C] 0.03～0.15%.The tapping later stage adds an amount of lime or synthetic slag.
(2) ladle refining: on ladle refining furnace (capacity and electric furnace are complementary), carry out the refining of molten steel, remove obnoxious flavour and inclusion in the steel, ladle is taken a seat, thermometric, analysis, according to circumstances adjusts argon pressure; Al to 0.050% is fed in LF deoxidation just, adds alloy block and vanadium iron, stirs 5～10 minutes, adjusts chemical ingredients and advances internal control.When molten steel thermometric temperature is 1630～1650 ℃, enter the vacuum degassing, vacuum tightness is 66.7Pa, keeps 20～25 minutes.Guarantee [H]≤0.00015%; All the components enters optimizes beginning bull ladle in the scope that requires, 1550～1570 ℃ of bull ladle temperature.
(3) continuous casting: high-temperature molten steel waters into tundish, 20～40 ℃ of tundish superheating temperature by protective casing in the ladle.Before tundish uses fully the cleaning, internal surface is as fire-resistant coating and the crack must not be arranged; Molten steel in the tundish is through continuous cast mold, and induction stirring is abundant, and pulling rate is slow, with rational speed, waters and outpours 140 * 140mm
2～450 * 450mm
2The qualified continuously cast bloom of cross dimensions is 0.9～2.10m/min according to different ingot shape size pouring speeds.Qualified continuously cast bloom is chilled to 900 ℃ soon on cold bed, advance the burial pit slow cooling, and the slow cooling time is 36～50 hours.
Second step: rod iron is rolling
Adopt rolling mill hot-work rolling method, earlier qualified continuously cast bloom surface cleared up, again its hot-work is rolling to the finished product rod iron, technology point:
1. process furnace heating process: 1150～1200 ℃ of soaking temperatures, 3～4 hours heat tracing time, 1130～1200 ℃ of steel billet tapping temperatures, the male and female face temperature difference≤30 ℃; (conventional this series structure steel soaking temperature is 1130～1180 ℃, soaking time 2 hours 30 minutes, 1130～1180 ℃ of tapping temperatures, the technical program is compared soaking temperature with prior art and is improved 20 ℃, to implement the diffusion process of steel billet heating, help improving the homogeneity of ingredients and the tissue homogeneous degree of continuously cast bloom.
2. controlled rolling technology: after the steel billet of homogeneous heating is come out of the stove, normally open the high pressure descaling machine, 1130～1180 ℃ of start rolling temperatures, 760～800 ℃ of finishing temperatures.
3. cooling control technology: wear and be water-cooled to 500～600 ℃ of surface temperatures, air cooling again.(the conventional structure steel does not adopt this technology for controlled cooling).
The 3rd step: rod iron annealing
680～710 ℃ of annealing temperatures, 8～12 hours hold-times, tapping temperature≤250 ℃, air cooling, wind sheltering.
The C level ring chain steel that is obtained by method of the present invention has following characteristics:
1. C level ring chain steel clarity height of the present invention: inclusion rank low (A2B2C1D1), gas content (oxygen≤15ppm, hydrogen≤1.5ppm).
2. C level ring chain steel homogeneous microstructure of the present invention is careful, is globular pearlite, and hardness is evenly moderate, and at HBW185-211, autstenitic grain size is narrower than 7 grades.
3. C level ring chain steel of the present invention is heat-treated (870～890 ℃ of shrend+380～420 ℃ tempering) on Equipment for Heating Processing can obtain good comprehensive mechanical performance: tensile strength (Rm) 〉=1300MPa, yield strength (ReL) 〉=1150MPa, unit elongation (A) 〉=10%, relative reduction in area (Z) 〉=50%, impelling strength (Akv) 〉=40J.
Description of drawings
Fig. 1 is the microstructure picture of steel of the present invention under 500 times.
Embodiment
Below describe the present invention in detail by specific embodiment.
The chemical ingredients of the embodiment of the invention is as shown in table 2.
The preparation method of the embodiment of the invention adopts the three-steps process flow process: the first step: electric arc furnace just refines → ladle furnace vacuum refinement → continuous casting; Second step: rolling mill hot-work is rolled into rod iron; The 3rd step: rod iron annealing.Its concrete processing condition are as shown in table 3.
The performance of the embodiment of the invention is as shown in table 4.
The chemical ingredients of table 2 embodiment rod iron, wt%
Table 3
Table 4
Table 5 is comparing results of the mechanical performance index of product performance of the present invention and GB requirement and imported materials and items requirement:
Table 5
| Tensile strength MPa | Yield strength MPa | Elongation % | Relative reduction in area % | Impelling strength J | |
| Rigidity energy of the present invention | ≥1300 | ≥1150 | ≥14 | ≥55 | (Akv)≥45 |
| Import 23MnNiMoCr54 | ≥1180 | ≥980 | ≥10 | ≥50 | (Akv)≥40 |
| The steel requirement | |||||
| The GB/T10560 standard-required | ≥1080 | ≥885 | ≥10 | ≥50 | (Aku)≥35 |
Table 6 is chemical ingredients and performances of import steel and imitation import steel.
Table 6
Every index correlation data of the mechanical property of C level round-link chain of the present invention and GB/T12718 such as following table 7, ring chain steel of the present invention has good fatigue property and welding property simultaneously.
Table 7
| Breaking load KN | Minimum percentage of total elongation when disrumpent feelings, % | Maximum elongation rate under the test load, % | Fatigue life cycle ten thousand times | |
| The GB/T12718 standard-required | >800 | ≥12 | ≤1.6 | ≥3 |
| φ 30mm steel of the present invention | 1384 | 15.40 | 1.11 | 3.67 |
| φ 34mm steel of the present invention | 1670 | 12.8 | 1.21 | 3.90 |
Fig. 1 is the microstructure picture of steel of the present invention under 500 times.Be organized as globular pearlite among the figure, tissue distribution is even, and the tissue of the type plays important effect for the intensity and the toughness that improve the invention steel, thereby has improved the fatigue property of round-link chain.
More than by embodiment the present invention has been described in more detail, but these embodiment do not constitute any limitation of the invention, under the prerequisite that does not break away from design of the present invention, more other equivalent embodiment can also be arranged.
Claims (7)
1. high toughness ring chain steel for mine, its chemical ingredients by weight percentage is:
Carbon: 0.20～0.26%,
Manganese: 1.10～1.40%,
Nickel: 0.85～1.15%,
Chromium: 0.40～0.60%,
Molybdenum: 0.40～0.60%,
Vanadium: 0.03～0.10%,
Aluminium: 0.020～0.050%,
Silicon :≤0.25%,
Copper :≤0.25%,
Sulphur :≤0.020%,
Phosphorus :≤0.020%,
All the other are Fe and unavoidable impurities.
2. high toughness ring chain steel for mine according to claim 1 is characterized in that, described nickel content is 0.90～1.10%.
3. the manufacture method of a high toughness ring chain steel for mine comprises:
Arc melting routinely, refinery practice and given alloying element ratio adopt continuous casting process to produce strand;
The continuous-cast blank soaking temperature: 1150～1200 ℃, 1130～1180 ℃ of start rolling temperatures, 760～800 ℃ of finishing temperatures;
Wear water cooling after rolling, again air cooling;
Rolled steel bar is annealed, 680～710 ℃ of annealing temperatures, 8～12 hours hold-times, tapping temperature≤250 ℃, air cooling, wind sheltering.
4. the manufacture method of high toughness ring chain steel for mine according to claim 3 comprises the steps:
First step carries out molten steel and just refines, ladle refining, and continuous casting, produce strand:
(1) molten steel just refines: the tapping condition: 1630～1650 ℃ of temperature; [P]≤0.010%, [C] 0.03～0.15%;
(2) ladle refining: when molten steel thermometric temperature is 1630～1650 ℃, enter the vacuum degassing, vacuum tightness is 66.7Pa, keeps 20～25 minutes, guarantees [H]≤0.00015%; All the components enters optimizes beginning bull ladle in the scope that requires, 1550～1570 ℃ of bull ladle temperature;
(3) continuous casting: high-temperature molten steel waters into tundish, 20～40 ℃ of tundish superheating temperature by protective casing in the ladle; Pouring speed is 0.9～2.10m/min; Cool off laggard burial pit slow cooling;
Second step, rod iron is rolling
(1) process furnace heating process: 1150～1200 ℃ of soaking temperatures, 3～4 hours heat tracing time, 1130～1200 ℃ of steel billet tapping temperatures;
(2) controlled rolling technology: 1130～1180 ℃ of start rolling temperatures, 760～800 ℃ of finishing temperatures;
(3) cooling control technology: be cooled to 500～600 ℃ of surface temperatures, again air cooling;
Third step, rod iron annealing
680～710 ℃ of annealing temperatures, 8～12 hours hold-times, tapping temperature≤250 ℃, air cooling, wind sheltering.
5. the manufacture method of high toughness ring chain steel for mine according to claim 4 is characterized in that, in the described continuous casting step, the qualified continuously cast bloom after the cast is chilled to 900 ℃ soon on cold bed.
6. the manufacture method of high toughness ring chain steel for mine according to claim 4 is characterized in that, the described time of advancing the burial pit slow cooling is 36～50 hours.
7. the manufacture method of high toughness ring chain steel for mine according to claim 4 is characterized in that, in the described process furnace complete processing, and the male and female face temperature difference≤30 ℃
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2007100463959A CN101397636B (en) | 2007-09-25 | 2007-09-25 | High toughness ring chain steel for mine and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2007100463959A CN101397636B (en) | 2007-09-25 | 2007-09-25 | High toughness ring chain steel for mine and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101397636A true CN101397636A (en) | 2009-04-01 |
| CN101397636B CN101397636B (en) | 2010-12-01 |
Family
ID=40516477
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2007100463959A Expired - Fee Related CN101397636B (en) | 2007-09-25 | 2007-09-25 | High toughness ring chain steel for mine and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101397636B (en) |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101880838A (en) * | 2010-06-13 | 2010-11-10 | 齐齐哈尔轨道交通装备有限责任公司 | Steel and car coupler made of steel |
| CN101942608A (en) * | 2010-09-30 | 2011-01-12 | 南京钢铁股份有限公司 | Steel for offshore mooring chain |
| WO2011156983A1 (en) * | 2010-06-13 | 2011-12-22 | 齐齐哈尔轨道交通装备有限责任公司 | Method for producing steel |
| CN103276303A (en) * | 2013-06-07 | 2013-09-04 | 南京钢铁股份有限公司 | High strength chain steel for mine, and preparation method thereof |
| CN103451554A (en) * | 2013-09-03 | 2013-12-18 | 上海清河机械有限公司 | Metal material for valve box, and preparation method thereof |
| CN104532143A (en) * | 2014-12-22 | 2015-04-22 | 江阴兴澄特种钢铁有限公司 | Mining large-specification and high-strength chain steel and preparation method thereof |
| CN106498116A (en) * | 2016-10-27 | 2017-03-15 | 首钢水城钢铁（集团）有限责任公司 | A kind of production technology of circle chain of mine steel |
| CN108148970A (en) * | 2017-12-21 | 2018-06-12 | 燕山大学 | A kind of method that high-tensile round-link chain steel obtains globular carbide tissue |
| CN110714164A (en) * | 2019-11-08 | 2020-01-21 | 西宁特殊钢股份有限公司 | High-quality Cr54 steel for coal mine chain ring and production method thereof |
| CN111560499A (en) * | 2020-05-18 | 2020-08-21 | 南京钢铁股份有限公司 | Annealing process of steel for high-strength-grade mining chain |
| CN111575590A (en) * | 2020-06-24 | 2020-08-25 | 江苏利淮钢铁有限公司 | Steel for tricone bit leg and preparation method thereof |
| CN114657334A (en) * | 2022-03-25 | 2022-06-24 | 西宁特殊钢股份有限公司 | Annealing process of mining circular chain steel 23MnNiMoCr54 with both structure control and hardness control |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2139115A1 (en) * | 1971-08-04 | 1973-02-15 | Carl Clarus | Boron contg steels - for use as heavy duty round-link chains |
| DE10105809C1 (en) * | 2001-02-08 | 2002-07-18 | Thiele Gmbh & Co Kg | Production of a round link chain made from heat-treatable steel, used in drive and conveying elements, comprises forming a chain strand, heat treating while calibrating the chain and post-treating |
| CN100420765C (en) * | 2006-03-07 | 2008-09-24 | 河北工业大学 | Steel for circular ring chains for mineral purpose |
| CN100513616C (en) * | 2006-04-07 | 2009-07-15 | 宣化钢铁集团有限责任公司 | Low-cost steel for circular chain for mine and production process thereof |
| CN1908216A (en) * | 2006-08-09 | 2007-02-07 | 河北正同科技开发有限公司 | Steel for C grade circle chain of mine |
-
2007
- 2007-09-25 CN CN2007100463959A patent/CN101397636B/en not_active Expired - Fee Related
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101880838A (en) * | 2010-06-13 | 2010-11-10 | 齐齐哈尔轨道交通装备有限责任公司 | Steel and car coupler made of steel |
| WO2011156983A1 (en) * | 2010-06-13 | 2011-12-22 | 齐齐哈尔轨道交通装备有限责任公司 | Method for producing steel |
| CN101942608A (en) * | 2010-09-30 | 2011-01-12 | 南京钢铁股份有限公司 | Steel for offshore mooring chain |
| CN103276303A (en) * | 2013-06-07 | 2013-09-04 | 南京钢铁股份有限公司 | High strength chain steel for mine, and preparation method thereof |
| CN103451554A (en) * | 2013-09-03 | 2013-12-18 | 上海清河机械有限公司 | Metal material for valve box, and preparation method thereof |
| CN103451554B (en) * | 2013-09-03 | 2015-07-29 | 上海清河机械有限公司 | A kind of clack box metallic substance and preparation method thereof |
| CN104532143A (en) * | 2014-12-22 | 2015-04-22 | 江阴兴澄特种钢铁有限公司 | Mining large-specification and high-strength chain steel and preparation method thereof |
| CN104532143B (en) * | 2014-12-22 | 2016-11-16 | 江阴兴澄特种钢铁有限公司 | A kind of mining big specification, high-test chain steel and preparation method thereof |
| CN106498116A (en) * | 2016-10-27 | 2017-03-15 | 首钢水城钢铁（集团）有限责任公司 | A kind of production technology of circle chain of mine steel |
| CN108148970A (en) * | 2017-12-21 | 2018-06-12 | 燕山大学 | A kind of method that high-tensile round-link chain steel obtains globular carbide tissue |
| CN110714164A (en) * | 2019-11-08 | 2020-01-21 | 西宁特殊钢股份有限公司 | High-quality Cr54 steel for coal mine chain ring and production method thereof |
| CN110714164B (en) * | 2019-11-08 | 2020-11-06 | 西宁特殊钢股份有限公司 | High-quality Cr54 steel for coal mine chain ring and production method thereof |
| CN111560499A (en) * | 2020-05-18 | 2020-08-21 | 南京钢铁股份有限公司 | Annealing process of steel for high-strength-grade mining chain |
| CN111560499B (en) * | 2020-05-18 | 2022-03-22 | 南京钢铁股份有限公司 | Annealing process of steel for high-strength-grade mining chain |
| CN111575590A (en) * | 2020-06-24 | 2020-08-25 | 江苏利淮钢铁有限公司 | Steel for tricone bit leg and preparation method thereof |
| CN114657334A (en) * | 2022-03-25 | 2022-06-24 | 西宁特殊钢股份有限公司 | Annealing process of mining circular chain steel 23MnNiMoCr54 with both structure control and hardness control |
| CN114657334B (en) * | 2022-03-25 | 2023-11-17 | 西宁特殊钢股份有限公司 | Annealing process of mining round-link chain steel 23MnNiMoCr54 with structure control and hardness control |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101397636B (en) | 2010-12-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101397636B (en) | High toughness ring chain steel for mine and method for producing the same | |
| CN102618792B (en) | High-strength abrasion-resistant steel for engineering machinery and manufacturing method thereof | |
| CN101289731B (en) | CrMnTi narrow hardenability strip pinion steels and method of manufacture | |
| CN102703817B (en) | Free-machining pinion steel and production technique thereof | |
| CN101775558B (en) | Fe-Cr-B cast abrasion-resistant alloy and manufacturing method thereof | |
| CN100420765C (en) | Steel for circular ring chains for mineral purpose | |
| CN104294153B (en) | A kind of alkali resistance corrosion anchor steel and production method | |
| CN100467652C (en) | Easy-weld hardening high-strength steel plate and production method thereof | |
| CN102703816B (en) | High-carbon low-alloy wear-resistant ball steel and production process thereof | |
| CN103966515B (en) | A kind of method utilizing electric arc furnace to prepare low-alloy high-strength toughness cast steel adding | |
| CN105525226A (en) | Martensitic stainless steel wire rod and production method thereof | |
| CN106939391A (en) | A kind of Ca microalloyings easy-cutting high strength fractured connecting rod steel and manufacture method | |
| CN101016603A (en) | High-boron cast steel containing granular boride and preparing method thereof | |
| CN109023119A (en) | A kind of abrasion-resistant stee and its manufacturing method with excellent plasticity and toughness | |
| CN102703822B (en) | Preparation method of high-speed steel for composite roll collar | |
| CN103556069A (en) | Large-diameter seamless steel tube for high-pressure gas cylinders and manufacturing method thereof | |
| CN102925783A (en) | Method for preparing hypereutectic high chromium white cast iron | |
| CN106191650A (en) | High abrasion Surface hardened layer type gren rod and production method thereof | |
| CN102691005A (en) | Low alloy die steel | |
| CN114672723B (en) | 46MnVS series steel for expansion connecting rod and manufacturing method thereof | |
| CN103451398A (en) | Manufacture method of 50CrVA alloy structural steel type hot rolled round steel bar | |
| CN102424936A (en) | Low temperature impact resistance allay structure steel and manufacture method thereof | |
| CN100999800A (en) | Casting steel containing rare earth element and protuction process thereof | |
| CN100513616C (en) | Low-cost steel for circular chain for mine and production process thereof | |
| CN103993219A (en) | High-toughness synthetic cast iron cylinder-sleeve material and manufacturing process |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| ASS | Succession or assignment of patent right |
Owner name: BAOSTEEL SPECIAL STEEL CO., LTD. Free format text: FORMER OWNER: BAOSHAN IRON + STEEL CO., LTD. Effective date: 20131211 |
|
| C41 | Transfer of patent application or patent right or utility model | ||
| COR | Change of bibliographic data |
Free format text: CORRECT: ADDRESS; FROM: 201900 BAOSHAN, SHANGHAI TO: 200940 BAOSHAN, SHANGHAI |
|
| TR01 | Transfer of patent right |
Effective date of registration: 20131211 Address after: 200940 Baoshan District aquatic Road, Shanghai, No. 1269 Patentee after: BAOSTEEL SPECIAL STEEL Co.,Ltd. Address before: 201900 Fujin Road, Shanghai, orchard, Baoshan District Patentee before: BAOSHAN IRON & STEEL Co.,Ltd. |
|
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20101201 Termination date: 20210925 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |