CN105002439B - A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method - Google Patents
A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method Download PDFInfo
- Publication number
- CN105002439B CN105002439B CN201510459563.1A CN201510459563A CN105002439B CN 105002439 B CN105002439 B CN 105002439B CN 201510459563 A CN201510459563 A CN 201510459563A CN 105002439 B CN105002439 B CN 105002439B
- Authority
- CN
- China
- Prior art keywords
- steel
- wear
- temperature
- brinell hardness
- quenching
- 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
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses the grade wear-resisting steel of Brinell hardness 400 and its manufacture method, the chemical composition of steel is by mass percentage：C 0.14~0.21%, Si 0.20~0.40%, Mn 0.9~1.4%, P≤0.015%, S≤0.008%, Cr 0.5~0.8%, Ni 0.05~0.08%, Mo 0.2~0.4, Als 0.02~0.05%, Ti 0.02~0.03, V≤0.02%, B≤0.005%, remaining is iron and inevitable impurity.Manufacture method comprises the following steps：Vacuum metling is carried out by proportioning chemical composition and is cast into base, then carries out heating of plate blank, rolling, cooling, quenching, the obtained steel plate finished product of lonneal processing again.The residual stress uniformity of this abrasion-resistant stee is good, does not ftracture and deforms in use, wear-resisting, service life length.
Description
Technical field
The invention belongs to steel and iron manufacturing field, and in particular to a kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method.
Background technology
Abrasion-resistant stee is a kind of ferrous materials being widely used under various wear working conditions, and its object is to slow down mechanical part
Attrition, improve life-span of product, the time of failure behaviour occurs because of abrasion for prolonged mechanical product, it is desirable to has higher
Hardness number to ensure the wear resistance under bad working environments.
Residual stress is to influence the key parameter that abrasion-resistant stee uses, and is had directly with the cracking of steel plate and the wearability on surface
Relation.And common abrasion-resistant stee hardness number is high, its interior residual stress is big, and uniformity is bad, it is easy to occurs in use
The problem of steel plate ftractures；In addition, the residual stress on surface also has certain relation with wearability, surface of steel plate if compression,
Then there is castering action to the anti-wear performance and fatigue behaviour that improve steel plate.
The content of the invention
It is an object of the invention to provide a kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method, manufacture method to pass through
There is the control of the elements such as important chemical composition C, Si, Mn, Cr, B of considerable influence to residual stress, and use and reasonably quench,
Tempering heat treatment process, make abrasion-resistant stee while excellent wear and higher toughness is possessed, have uniformly to press on its surface and answer
Power, further enhance its anti-wear performance and anti-fatigue performance；The residual stress uniformity of this abrasion-resistant stee is good, in use not
Generation is ftractureed and deformation, wear-resisting, service life length.
What the present invention was realized in：
A kind of grade wear-resisting steel of Brinell hardness 400, the chemical composition of steel are by mass percentage：C 0.14~0.21%, Si
0.20~0.40%, Mn 0.9~1.4%, P≤0.015%, S≤0.008%, Cr 0.5~0.8%, Ni 0.05~
0.08%, Mo 0.2~0.4, Als 0.02~0.05%, Ti 0.02~0.03, V≤0.02%, B≤0.005%, remaining is
Iron and inevitable impurity.
Carbon (C) content of the present invention is 0.14~0.21%.Carbon is to influence wear-resisting hardness of steel, hardness, toughness and quenching degree
Important element, and influence the mostly important element of steel microscopic structure；As carbon content increases, the hardness increase of steel, impact
Toughness is remarkably decreased, and wearability gradually steps up；Carbon content is too high, and the carbide content in steel is excessive, and what is formed after heat treatment is high
Carbon lamellar martensite, the hardness of steel is high and toughness is low, and is easily ftractureed in heat treatment process；Carbon content is too low, the hardenability of steel
Deficiency, hardness is too low, wearability deficiency.
Silicon (Si) content of the present invention is 0.20~0.40%.In steelmaking process, silicon is used as reducing agent and deoxidier.Silicon
It is non-carbide former, is to be present in ferrite or austenite in the form of solid solution.Therefore can be carried with reinforced ferrite
Gao Gang intensity and hardness, while the critical cooling rate of steel can be reduced, improve the quenching degree of steel.Silicon can also improve returning for steel
Fiery stability and inoxidizability, it is improved in steel, and the intensity of solid solution and the effect of cold deformation hardening ratio are extremely strong, are only second to
Phosphorus, but also reduce the toughness and plasticity of steel to a certain extent simultaneously.In addition, silicon makes steel be in banded structure, make the transverse direction of steel
Performance is less than longitudinal performance.But silicone content is too high to occur granular ferrite, reduce the toughness of steel and be also easy to produce hardening flaw；
And retained austenite dramatically increases, make the hardness of steel reduce.When the content of silicon is higher, cementite (Fe may be made3C) divide
Solution, make carbon free and exist in non-graphitic state, that is, have so-called graphitizing.In annealing, surface also easy decarburization.
The content of the manganese (Mn) of the present invention is 0.9~1.4%.Manganese is good deoxidier and desulfurizing agent, can eliminate or subtract
The weak red brittleness caused by sulphur, so as to improve the hot-working character of steel.Manganese and iron form solid solution, improve in steel ferrite and
The hardness and intensity of austenite, strengthen matrix；It is again simultaneously carbide former, substitutes a part of iron former into cementite
Son, generation manganess carbide (Mn3C), it is with cementite (Fe3C it) can be mutually dissolved, be formed in steel in alloy (carbide (Fe Mn)3C-type compound), so as to improve the intensity of steel, hardness and wearability.Manganese can reduce critical cooling rate, promote the geneva bodily form
Into improving the quenching degree of steel.Manganese, due to reducing critical transition temperature, plays a part of refining pearlite, also indirectly in steel
Play a part of improving pearlitic steel intensity.Manganese expands the γ phase regions in carbon iron balance phasor, and it makes steel formation and stable Ovshinsky
The ability of body tissue is only second to nickel.It is easy to get after quenching to martensitic structure.But manganese is superheated susceptivity element, heating temperature during quenching
Coarse grains can be caused by spending height；Manganese segregation coefficient in solidification is larger, it is easy in Grain Boundary Segregation, the performance of steel is produced not
Profit influences, and can cause remained austenite content increase in the quenching structure of steel, so manganese content control is between 0.9~1.4%.
Content≤0.015% of the phosphorus (P) of the present invention, content≤0.008% of sulphur (S).Sulphur, which is present in steel, to be made
Steel becomes hot-short, and phosphorus is also easy to produce segregation in crystallization process, so as to which the regional area generation in steel is cold short.Sulphur, phosphorus for
It is objectionable impurities elements for abrasion-resistant stee residual stress control, should do the best elimination.
The content of the chromium (Cr) of the present invention is 0.5~0.8%.Chromium is advantageous to the shape of the solution strengthening of steel and suitable carbide
Into, and then improve elevated temperature strength, hardness and the anti-wear performance of steel.Chromium increase steel quenching degree, especially with manganese, the reasonably combined energy of silicon
Quenching degree is greatly improved, but also increases steel belt roof bolt fragility tendency simultaneously.Chromium can be solid-solution in ferrite and produce solution strengthening
Effect, improve the tensile strength and yield point of weld metal.But its content is more than 0.8%, under weld metal toughness can be made obvious
Drop.
The content of the nickel (Ni) of the present invention is 0.05~0.08%.Nickel and carbon do not form carbide, are to form and stablize Austria
The main alloy element of family name's body, quenching degree can be improved by adding certain nickel, the tissue of steel is retained a small amount of remaining Austria at normal temperatures
Family name's body, to improve its toughness.Nickel element can improve the impact flexibility of steel in itself, and the low-temperature impact especially to steel improves
It is larger.
The content of the molybdenum (Mo) of the present invention is 0.2~0.4.Molybdenum is deposited in steel in the form of solid solution phase and Carbide Phases
.Critical cooling rate can be reduced, promotes martensite to be formed, improves the quenching degree of steel.Molybdenum carbide (MoC) is formed with carbon (C), is carried
Gao Gang hardness；And matrix is strengthened by solution strengthening, the density of hardening phase is improved, while also improve the stabilization of carbide
Property, favourable effect is produced to the intensity of steel.Influence of the molybdenum to temper brittleness is rather complicated, is deposited as single alloying element
Steel belt roof bolt fragility is being improved, but when causing the element of temper brittleness with other and depositing, molybdenum reduces or suppressed other elements institute again
Caused temper brittleness.
The content of the dissolved aluminum (Als) of the present invention is 0.02~0.05%.A small amount of dissolved aluminum is added in steel, can be refined
Crystal grain, improve impact flexibility.
The content of the titanium (Ti) of the present invention is 0.02~0.03.Titanium improves the strong of steel by crystal grain thinning and precipitation strength
Degree, titanium generates titanium carbide (TiN) particle of disperse under continuous casting cooling condition, because its fusing point is very high, welding heat affected
Area can significantly inhibit crystal grain and grow up, and add trace amount of titanium to significantly improve the toughness of heat affected area.
Content≤0.02% of the vanadium (V) of the present invention.Vanadium improves the intensity of steel, appropriate content of vanadium energy by crystal grain thinning
The wearability of matrix is enough improved, but the increase On Impact Toughness of content of vanadium also has an impact.
Content≤0.005% of the boron (B) of the present invention.Micro boron can be adsorbed on austenite grain boundary, reduce crystal boundary
Energy, improve the quenching degree of steel.
The present invention also provides the manufacture method of the above-mentioned grade wear-resisting steel of Brinell hardness 400, comprises the following steps：Ultra-clean steel work
Skill smelt → and desulfurizing iron → converter top bottom blowing → application of vacuum → is casting continuously to form slab → heating of plate blank → rolling
→ cooling → quenching → lonneal → steel plate finished product, wherein,
In heating of plate blank step, in order to ensure that microalloy element fully dissolves and has certain austenite crystal
Degree, reduce residual stress distribution inequality possibility, soaking temperature uses 1190 DEG C~1250 DEG C, and the rate of heat addition is 8~10min/
cm；
In milling step, start rolling temperature >=1050 DEG C of milling step, finishing temperature >=980 DEG C, single pass reduction ratio
More than 20%, minuent, which is suppressed, can refine steel plate center portion crystal grain so that tissue and residual stress distribution tend to be equal on sheet metal thickness
It is even；
In quenching Step, hardening heat is 870 DEG C, and soaking time is 1.0~2.0min/mm* thicknesss of slab；
In lonneal step, temperature is 190 DEG C, and soaking time is 3~4min/mm* thicknesss of slab, and lonneal is protected
The stress that presses to of plate surface is stayed, sufficient tempering time plays important work for the homogenization of residual stress distribution in sheet material
With obtaining tempered martensite after tempering.
This method is carried out vacuum metling and being cast into base by proportioning chemical composition, then again by heating of plate blank to 1190 DEG C~
1250 DEG C, followed by rolling, room temperature is cooled to, the preferable steel of wearability is obtained followed by quenching and lonneal
Plate, what lonneal remained plate surface presses to stress, and the anti-wear performance and fatigue behaviour for improving steel plate are obviously improved
Effect.
The present invention ensure that abrasion-resistant stee superficial hardness number 390 or so, tensile strength is about while residual stress is optimized
1300Mpa, there is higher case hardness, ensure that its anti-wear performance, there is higher tensile strength and preferable toughness；Fill
The tempering time divided make it that residual stress is more uniform in sheet material, advantageously reduces the tearing tendency of sheet material.
Carbon (C) content is 0.14~0.21% in the present invention, and carbon content is too high, then the hardness of steel is high and toughness is low, at heat
Easily ftractureed during reason, carbon content is too low, and the hardenability deficiency of steel, hardness is too low, wearability deficiency.Contain in composition
Mn, Cr, Ni, B element can improve the quenching degree of steel, so as to reduce residual stress gradient of the product in thickness direction, suppress out
Split.Ti, Als, V in composition play Grain refinement, make in steel residual stress distribution evenly.
The beneficial effects of the present invention are：
(1) in heating of plate blank step, soaking temperature uses 1190 DEG C~1250 DEG C, and the rate of heat addition is 8~10min/cm,
It ensure that microalloy element fully dissolves, and make slab that there is certain autstenitic grain size, reduce residual stress distribution not
Equal possibility；
(2), in the operation of rolling, single pass reduction ratio is more than 20%, can refine steel plate center portion crystal grain, make sheet metal thickness
Upper tissue and residual stress distribution are uniform；
(3), in lonneal, temperature is 190 DEG C, and soaking time is that every 1 millimeter of thickness of slab is incubated 3~4 minutes.Low temperature
Tempering remains the stress that presses to of plate surface, and sufficient tempering time plays for the homogenization of residual stress distribution in sheet material
Important function, steel plate obtains tempered martensite after tempering, adds wearability；
(4) Mn, Cr for, containing in steel plate composition, Ni, B element can improve the quenching degree of steel, so as to reduce product in thickness
The residual stress gradient in direction is spent, suppresses cracking；Ti, Als, V in composition play Grain refinement, make residual stress in steel
It is more evenly distributed.
Brief description of the drawings
Fig. 1 is the residual stress point layout figure using the steel plate obtained after this method.
Embodiment
The present invention is described further below in conjunction with the accompanying drawings.
Embodiment 1
A kind of thickness is the 30mm grade wear-resisting steel of Brinell hardness 400, and its chemical composition is by mass percentage：C
0.18%, Si 0.25%, Mn 1.05%, P 0.014%, S≤0.005%, Cr 0.78%, Ni 0.07%, Mo
0.31%, Als 0.038%, Ti 0.024%, V 0.013%, B 0.002, remaining is iron and inevitable impurity.
Vacuum metling is carried out by proportioning chemical composition and is cast into base, and slab is heated using 1200 DEG C of high temperature, added
Hot 240min；Then rolled again using 1060 DEG C of start rolling temperature, finishing temperature is 980 DEG C, using single pass reduction ratio
More than 20% pair slab rolls；Then cooled down；Sheet material after cooling is subjected to 870 DEG C of high temperature quenchings, insulation
30min；Sheet material after quenching is subjected to 190 DEG C of lonneals, 100min is incubated, completes the making of abrasion-resistant stee.Tables 1 and 2 point
It Wei not use thickness made from the above method should for the mechanical property table and surface residual of the 30mm grade wear-resisting steel of Brinell hardness 400
Power analytical table.
The mechanical property of table 1
The surface residual stress of table 2 (see Fig. 1)
Embodiment 2
A kind of thickness is the 20mm grade wear-resisting steel of Brinell hardness 400, and its chemical composition is by mass percentage：C
0.19%, Si 0.31%, Mn 1.2%, P 0.013%, S≤0.005%, Cr 0.68%, Ni 0.07%, Mo 0.29%,
Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, remaining is iron and inevitable impurity.
Vacuum metling is carried out by proportioning chemical composition and is cast into base, soaking is carried out to slab using 1200 DEG C, during heating
Between be 160min；Slab after heating is rolled, start rolling temperature is 1060 DEG C, and finishing temperature is 980 DEG C, single pass pressure
Rate is more than 20%；Cooling；Sheet material after cooling is subjected to 870 DEG C of high temperature quenchings, is incubated 20min；Sheet material after quenching is carried out
190 DEG C of lonneals, soaking time 70min, complete the making of abrasion-resistant stee.
Table 3 and table 4 are respectively to use mechanics of the thickness made from the above method for the 20mm grade wear-resisting steel of Brinell hardness 400
Performance table and surface residual stress analytical table.
The mechanical property of table 3
The surface residual stress of table 4
Embodiment 3
A kind of thickness is the 25mm grade wear-resisting steel of Brinell hardness 400, and its chemical composition is by mass percentage：C
0.17%, Si 0.31%, Mn 0.9%, P 0.013%, S≤0.008%, Cr 0.68%, Ni 0.07%, Mo 0.29%,
Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, remaining is iron and inevitable impurity.
Vacuum metling is carried out by proportioning chemical composition and is cast into base, soaking is carried out to slab using 1250 DEG C, during heating
Between be 200min；Slab after heating is rolled, start rolling temperature is 1200 DEG C, and finishing temperature is 980 DEG C, single pass pressure
Rate is more than 30%；Cooling；Sheet material after cooling is subjected to 870 DEG C of high temperature quenchings, is incubated 50min；Sheet material after quenching is carried out
190 DEG C of lonneals, soaking time 100min, complete the making of abrasion-resistant stee.
Table 5 and table 6 are respectively to use mechanics of the thickness made from the above method for the 25mm grade wear-resisting steel of Brinell hardness 400
Performance table and surface residual stress analytical table.
The mechanical property of table 5
The surface residual stress of table 6
Embodiment 4
A kind of thickness is the 22mm grade wear-resisting steel of Brinell hardness 400, and its chemical composition is by mass percentage：C
0.14%, Si 0.31%, Mn 0.9%, P 0.013%, S≤0.006%, Cr 0.68%, Ni 0.07%, Mo 0.29%,
Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, remaining is iron and inevitable impurity.
Vacuum metling is carried out by proportioning chemical composition and is cast into base, soaking is carried out to slab using 1250 DEG C, during heating
Between be 176min；Slab after heating is rolled, start rolling temperature is 1200 DEG C, and finishing temperature is 980 DEG C, single pass pressure
Rate is more than 30%；Cooling；Sheet material after cooling is subjected to 870 DEG C of high temperature quenchings, is incubated 33min；Sheet material after quenching is carried out
190 DEG C of lonneals, soaking time 77min, complete the making of abrasion-resistant stee.
Table 7 and table 8 are respectively to use mechanics of the thickness made from the above method for the 22mm grade wear-resisting steel of Brinell hardness 400
Performance table and surface residual stress analytical table.
The mechanical property of table 7
The surface residual stress of table 8
From table 1 to table 8 as can be seen that using this method while residual stress is optimized, it ensure that wear-resisting steel surface is hard
Angle value is 390 or so, tensile strength about 1300Mpa, and -20 DEG C of ballistic works ensure more than 30J, therefore with higher case hardness
Its anti-wear performance, while there is higher tensile strength and preferable toughness.
The Wuhan Iron and Steel Plant wear-resisting output of steel of the rank of Brinell hardness 400 in 2014 is about 8000 tons, and the turnover is about 48,000,000 yuan.This hair
It is bright to prevent product from ftractureing, hence it is evident that to improve Wear Resistance energy and fatigue behaviour, only calculate, produce by 1% marginal benefit
Ten thousand yuan of * 1%=48 of about 48,000,000 yuan of benefit are annual.
Claims (1)
1. a kind of manufacture method of the grade wear-resisting steel of Brinell hardness 400, comprises the following steps：Ultra-clean steel technique carries out smelting → iron
Water desulfurization → converter top bottom blowing → application of vacuum → be casting continuously to form slab → heating of plate blank → rolling → cooling → quenching →
Lonneal → steel plate finished product, it is characterised in that：
The chemical composition of the grade wear-resisting steel of Brinell hardness 400 is by mass percentage：C 0.21%, Si 0.20~0.40%,
Mn1.05~1.4%, P 0.013~0.015%, S 0.006~0.008%, Cr 0.5~0.8%, Ni 0.05~
0.08%, Mo0.2~0.4%, Als 0.02~0.05%, Ti 0.024~0.03%, V≤0.02%, B≤0.005%, its
Yu Weitie and inevitable impurity；
In heating of plate blank step, soaking temperature is 1190 DEG C~1250 DEG C, and the rate of heat addition is 8~10min/cm；
In milling step, start rolling temperature >=1050 DEG C of milling step, finishing temperature >=980 DEG C, single pass reduction ratio is more than
20%；
In quenching Step, hardening heat is 870 DEG C, and soaking time is 1.0~2.0min/mm* thicknesss of slab；
In lonneal step, temperature is 190 DEG C, and soaking time is 3~4min/mm* thicknesss of slab.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510459563.1A CN105002439B (en) | 2015-07-30 | 2015-07-30 | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510459563.1A CN105002439B (en) | 2015-07-30 | 2015-07-30 | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105002439A CN105002439A (en) | 2015-10-28 |
| CN105002439B true CN105002439B (en) | 2017-11-17 |
Family
ID=54375295
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510459563.1A Active CN105002439B (en) | 2015-07-30 | 2015-07-30 | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105002439B (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105821300A (en) * | 2016-04-08 | 2016-08-03 | 太仓市沪太热处理厂 | Heat treatment process of low-alloy large mold steel |
| CN105970110A (en) * | 2016-05-04 | 2016-09-28 | 武汉钢铁股份有限公司 | Low-alloy high-strength abrasion-resistant steel and preparation method thereof |
| CN106244920B (en) * | 2016-08-08 | 2019-01-22 | 武汉钢铁有限公司 | 450 grade wear-resisting steel of Brinell hardness and its manufacturing method |
| CN107217202B (en) * | 2017-07-19 | 2019-06-25 | 武汉钢铁有限公司 | A kind of 500 grades of Brinell hardness of abrasion-resistant stee and its manufacturing method |
| CN110184545B (en) * | 2019-05-24 | 2020-11-20 | 武汉钢铁有限公司 | Low-temperature semi-through quenched wear-resistant steel with Brinell hardness of 400HB and production method thereof |
| CN110527808B (en) * | 2019-08-26 | 2021-05-18 | 武汉科技大学 | Low-temperature residual stress regulation and control method for hot-rolled high-strength strip steel |
| CN110646306B (en) * | 2019-11-06 | 2022-10-11 | 湖南华菱湘潭钢铁有限公司 | Method for evaluating segregation of continuous casting billet through hardness |
| CN111621717A (en) * | 2020-07-17 | 2020-09-04 | 攀钢集团研究院有限公司 | Method for controlling surface hardness fluctuation of titanium-containing pickled plate |
| CN114770049B (en) * | 2022-05-13 | 2023-12-15 | 无锡华美新材料有限公司 | Manufacturing method of superhard template for manufacturing 5G communication PCB |
| CN114892089B (en) * | 2022-05-21 | 2023-09-05 | 湖南华菱湘潭钢铁有限公司 | Method for improving hardness uniformity of wear-resistant steel section |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002256382A (en) * | 2000-12-27 | 2002-09-11 | Nkk Corp | Wear resistant steel sheet and production method therefor |
| US9879334B2 (en) * | 2011-03-29 | 2018-01-30 | Jfe Steel Corporation | Abrasion resistant steel plate or steel sheet excellent in resistance to stress corrosion cracking and method for manufacturing the same |
| JP6007847B2 (en) * | 2013-03-28 | 2016-10-12 | Ｊｆｅスチール株式会社 | Wear-resistant thick steel plate having low temperature toughness and method for producing the same |
| CN103146997B (en) * | 2013-03-28 | 2015-08-26 | 宝山钢铁股份有限公司 | A kind of low-alloy high-flexibility wear-resistant steel plate and manufacture method thereof |
-
2015
- 2015-07-30 CN CN201510459563.1A patent/CN105002439B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN105002439A (en) | 2015-10-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105002439B (en) | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method | |
| CN104032221B (en) | A kind of Nb-microalloying high-carbon-chromium bearing steel and hot rolling production method thereof | |
| CN107217202B (en) | A kind of 500 grades of Brinell hardness of abrasion-resistant stee and its manufacturing method | |
| CN108179350A (en) | A kind of abrasion-resistant stee low cost short production cycle preparation method | |
| CN106244920B (en) | 450 grade wear-resisting steel of Brinell hardness and its manufacturing method | |
| CN108018492A (en) | A kind of Brinell hardness is more than the high-level low alloy wear resistance steel plate and manufacture method of 550HB | |
| CN106498294A (en) | A kind of high-level low-alloy wear-resistant steel of NM600 and its application | |
| CN103160738B (en) | A kind of low cost boron-containing steel and manufacture method thereof | |
| CN111809115B (en) | Super-thick plastic die steel with excellent impact corrosion wear resistance and preparation method thereof | |
| CN102676923A (en) | Steel with ultra-high thermal conductivity for hot-stamping die and preparation method of steel | |
| CN105039861B (en) | A kind of middle manganese boric low alloy wear resistant steel plate and preparation method thereof | |
| CN108396240A (en) | A kind of heat-resistant antifriction steel plate and its production method | |
| CN110184545A (en) | A kind of Brinell hardness is half through hardening abrasion-resistant stee of 400HB rank low temperature and production method | |
| CN102234743A (en) | Low carbon martensite steel plate and production method | |
| CN107130172B (en) | 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method | |
| CN106521338A (en) | High-strength high-hardness steel plate and flexibility production method | |
| CN108368591A (en) | Steel plate of pressure vessel and its manufacturing method with excellent post weld heat treatment patience | |
| CN106756489A (en) | 450 grades of anti-crack high-strength abrasion-proof steels of Brinell hardness and its manufacture method | |
| CN107881415B (en) | A kind of high temperature wear resistant steel plate and its manufacturing method | |
| CN109457184A (en) | A kind of high-wearing feature steel plate and its production method | |
| CN105970110A (en) | Low-alloy high-strength abrasion-resistant steel and preparation method thereof | |
| CN109609729A (en) | A kind of yield strength 650MPa grades of stainless steel plates and manufacturing method | |
| CN107557660B (en) | A kind of -50 DEG C of cryogenic steel of normalizing and its manufacturing method | |
| CN107675090A (en) | A kind of Brinell hardness 650HBW ranks high-wearing feature steel plate and preparation method thereof | |
| CN105483562A (en) | High-bending-resistance, high-strength and high-toughness die steel and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| TA01 | Transfer of patent application right | ||
| TA01 | Transfer of patent application right |
Effective date of registration: 20170824 Address after: 430083, Gate No. 2, Qingshan District, Hubei, Wuhan Applicant after: Wuhan iron and Steel Company Limited Address before: 430080 Wuhan, Hubei Friendship Road, No. 999, Wuchang Applicant before: Wuhan Iron & Steel (Group) Corp. |
|
| GR01 | Patent grant | ||
| GR01 | Patent grant |