CN107923023A - High rigidity steel plate and its manufacture method - Google Patents

High rigidity steel plate and its manufacture method Download PDF

Info

Publication number
CN107923023A
CN107923023A CN201680047778.5A CN201680047778A CN107923023A CN 107923023 A CN107923023 A CN 107923023A CN 201680047778 A CN201680047778 A CN 201680047778A CN 107923023 A CN107923023 A CN 107923023A
Authority
CN
China
Prior art keywords
steel plate
high rigidity
content
less
except
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
Application number
CN201680047778.5A
Other languages
Chinese (zh)
Other versions
CN107923023B (en
Inventor
林永禄
张浚相
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of CN107923023A publication Critical patent/CN107923023A/en
Application granted granted Critical
Publication of CN107923023B publication Critical patent/CN107923023B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The purpose of one aspect of the present invention is to provide high rigidity steel plate and its manufacture method, the high rigidity steel plate sets the composition of steel according to the relational expression of the minimum carbon content of the Brinell hardness for obtaining more than 500HB, so that the Brinell hardness with more than 500HB.One aspect of the present invention is related to high rigidity steel plate and its manufacture method, the high rigidity steel plate is by meeting following relational expressions (1) including the process cooled down to the hot rolled steel plate Jing Guo hot rolling come the high rigidity steel plate of the Brinell hardness with more than 500HB that manufactures, the minimum content of the carbon (C) of the high rigidity steel plate；[relational expression 1] C (minimum content of carbon (C)) >=0.481 0.104Mn 0.035Si 0.088Cr 0.054Ni 0.035Mo 0.0003C.R. are (wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, C.R. it is the value of cooling velocity when representing to cool down hot rolled steel plate, unit is DEG C/sec)；The high rigidity steel plate has the micro organization of the martensitic phase comprising more than 95 volume %, and the Brinell hardness with more than 500HB.

Description

High rigidity steel plate and its manufacture method
Technical field
The present invention relates to the high rigidity steel plate and its manufacture method for being used in various fields.
Background technology
The wearability and loading enabling capabilities of steel plate with high rigidity are excellent, so as to ensure long service life and Durability, and be used in various parts.
Especially, for abrasion-resistant stee, its grade is provided on the basis of Brinell hardness, is typically made into that (Bu Shi is hard from HB Degree) 350 grades to up to HB600 grades of various firmness levels.
In addition, the steel plate with high rigidity is at the same time with high intensity, so as to can also be used in as collided component, strengthening structure Part etc. is utilized in the field of high-strength structure, and has high economic value in terms of the lightweight of component and efficient activity.
For this high rigidity steel plate, generally during being cooled to room temperature from austenitic temperature domain, send out steel plate Life is mutually changed into martensite or bainite structure, so as to utilize high rigidity and intensity possessed by this low temperature phase change tissue.
But in order to obtain the desired hardness of each component, the various sides of control composition and technique are proposed in the prior art Case, but do not propose to obtain the benchmark of unified hardness.
The content of the invention
Technical problems to be solved
The purpose of one aspect of the present invention is to provide high rigidity steel plate, the steel plate utilize for obtain 500HB with On Brinell hardness minimum carbon content relational expression setting steel composition so that the Brinell hardness with more than 500HB.
The purpose of another aspect of the present invention is to provide the method for manufacture high rigidity steel plate, and the method is according to being used for The composition of the relational expression setting steel of the minimum carbon content of the Brinell hardness of more than 500HB is obtained, so as to manufacture with more than 500HB Brinell hardness high rigidity steel plate.
Technical solution
The preferable of the present invention is related to high rigidity steel plate on one side, it is by including to the hot rolled steel plate Jing Guo hot rolling The process cooled down is come the steel plate manufactured, and in terms of weight %, the steel plate is by carbon (C)：0.05~0.3%, silicon (Si)： Less than 0.5% (except 0%), manganese (Mn)：Less than 2.5% (except 0%), chromium (Cr)：Less than 1.5% (except 0%), molybdenum (Mo)：Less than 1.0% (except 0%), nickel (Ni)：Less than 1.0% (except 0%), niobium (Nb)：Less than 0.1% (except 0%), Titanium (Ti)：Less than 0.1% (except 0%), vanadium (V)：Less than 0.1% (except 0%), boron (B)：Less than 0.01% (except 0%), Aluminium (Al)：The iron (Fe) and other inevitable impurity compositions of less than 0.1% (except 0%), surplus；
The minimum content of the carbon (C) meets following relational expressions (1)；
[relational expression 1]
C (minimum content of carbon (C)) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
(wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to hot rolling The value of cooling velocity when steel plate is cooled down, unit are DEG C/sec)；
The steel plate has the micro organization of the martensitic phase comprising more than 95 volume %, and has more than 500HB's Brinell hardness.
The preferable method for being related to manufacture high rigidity steel plate on the other hand of the present invention, the method are by steel billet Carry out hot rolling and cooled down after hot rolled steel plate is made, so as to manufacture fine with the martensitic phase comprising more than 95 volume % The method of the steel plate of the Brinell hardness of tissue and more than 500HB, in terms of weight %, the steel billet is by carbon (C)：0.05~0.3%, Silicon (Si)：Less than 0.5% (except 0%), manganese (Mn)：Less than 2.5% (except 0%), chromium (Cr)：Less than 1.5% (0% removes Outside), molybdenum (Mo)：Less than 1.0% (except 0%), nickel (Ni)：Less than 1.0% (except 0%), niobium (Nb)：Less than 0.1% (0% Except), titanium (Ti)：Less than 0.1% (except 0%), vanadium (V)：Less than 0.1% (except 0%), boron (B)：Less than 0.01% (0% Except), aluminium (Al)：The iron (Fe) and other inevitable impurity compositions of less than 0.1% (except 0%), surplus；
The minimum content of the carbon (C) meets following relational expressions (1),
[relational expression 1]
C (minimum content of carbon (C)) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
(wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to hot rolling The value of cooling velocity when steel plate is cooled down, unit are DEG C/sec).
Beneficial effect
According to an aspect of the present invention, the present invention is to the micro organization with the martensitic phase comprising more than 95 volume % And the manufacture of the steel plate of the Brinell hardness of more than 500HB has effect that is more economical and can designing unified steel plate component.
Preferred forms
In order to obtain the hardness needed for each component, with high rigidity steel plate it is relevant propose in the prior art control composition and The various schemes of technique, but do not propose to obtain unified component benchmark of hardness etc..
Therefore, the present inventor in order to ensure high rigidity and intensity and by the micro organization of steel plate be formed as 95 volume % with On martensitic structure when, to condition of composition design for ensuring necessary firmness level etc. carried out study and test, And the present invention is completed based on its result.
That is, one of major technique thought of the invention is in order to ensure high rigidity and intensity and by the micro organization of steel plate When being formed as martensitic structures more than 95 volume %, it is proposed that for the bar for the composition design for ensuring necessary firmness level Part, so as to be manufactured more economically on the micro organization with martensitic phase comprising more than 95 volume % and more than 500HB The steel plate of Brinell hardness, and unified hardness can be obtained.
In the following, the steel plate of the preferable one side of the present invention is illustrated.
Carbon (C)：0.05~0.3 weight % (hereinafter referred to as " % ")
The content of carbon (C) can be 0.05~0.3%.
When the content of carbon is less than 0.05%, when being cooled down from austenite domain, it is difficult to martensitic traoformation occurs, also, When the content of carbon is more than 0.3%, increase the brittleness of steel, so as to be difficult to ensure that the stability of component.
The content of the carbon (C) can be 0.19~0.3%
Silicon (Si)：Less than 0.5% (except 0%)
The content of silicon (Si) can be less than 0.5% (except 0%).
Silicon increases the wearability of steel, therefore in terms of using the purposes of hardness, silicon is preferable alloying element.But When adding excessive Si, the surface characteristic and plating of steel are deteriorated, and can not realize complete Austria in the presence of when reheating The possibility of family name's body.
The content of the silicon (Si) can be 0.21~0.5%.The content of the silicon (Si) can be 0.253~ 0.34%.
Manganese (Mn)：Less than 2.5% (except 0%) and chromium (Cr)：Less than 1.5% (except 0%)
Manganese (Mn) and chromium (Cr) are the elements that martensitic transformation point is greatly reduced, and are usually making an addition to the element in steel In, the significant effect of the reduction transformation temperature of manganese and chromium and be only second to carbon, and manganese and chromium are low price elements, therefore be can economic profit Element.
The upper limit of the manganese content is preferably limited to 2.5%, and the upper limit of the chromium content is preferably limited to 1.5%.
When the too high levels of the manganese and chromium, at normal temperatures can retained austenite so that required in the presence of that can not obtain The possibility of the martensitic structure of more than 95 volume %.
The content of the manganese can be 1.4~2.5%.The content of the manganese can be 2.1~2.5%.
Molybdenum (Mo)：Less than 1.0% (except 0%) and nickel (Ni)：Less than 1.0% (except 0%)
Molybdenum (Mo) and nickel (Ni) are the elements for reducing martensite start temperature.
But the degree of the reduction martensite start temperature of molybdenum and nickel is less than Mn and Cr, and it is high valence elements, institute The upper limit for stating the additive amount of element is preferably limited to 1.0% respectively.
Niobium (Nb)：Less than 0.1% (except 0%) and titanium (Ti)：Less than 0.1% (except 0%)
Niobium (Nb) and titanium (Ti) can be added with the level of less than 0.1% (except 0%) respectively, and had and passed through Ovshinsky The miniaturization of body crystal grain improves the effect of the impact characteristics of steel plate.But fixed crystal boundary can be caused by adding excessive Nb and Ti The coarsening of Nb carbonitrides, so as to lose crystal grain micronized effect, therefore, the upper limit of niobium (Nb) and titanium (Ti) preferably limits respectively It is set to 0.1%.
In addition, in the case where adding B, in order to protect B from N and must to add the situation of Ti more, titanium (Ti) first with Carbon or nitrogen reaction in steel, form TiC or TiN, so as to improve the additive effect of boron (B).At this time, if the content and steel of titanium (Ti) In the content of nitrogen following relational expressions 2 are met based on Chemical Measurement, then the content of titanium is abundant.
[relational expression 2]
Ti (weight %)>N (weight %) × 3.42
Vanadium (V)：Less than 0.1% (except 0%)
Vanadium (V) can be added with the level of less than 0.1% (except 0%), by forming fine V carbide, be played The effect for being hardened by precipitation and preventing the physical property of weld part from reducing.
When the additive amount of vanadium is excessive, due to the coarsening of carbide, its effect is reduced, therefore, the upper limit of content of vanadium is excellent Choosing is limited to 0.1%.
Boron (B)：Less than 0.01% (except 0%)
Boron (B) can be added with the level of less than 0.01% (except 0%), and B is by hindering ferrite and pearlite Nucleation greatly improves the element of the quenching degree of steel, and when the thickness of steel is thick, the utilization rate of boron is very high.
In the present invention, in terms of the martensite of more than 95 volume % is obtained as final micro organization, to its manufacturing process Do not make special limitation, therefore, in order to ensure quenching degree, B can be added as needed.But when the content of B is excessive When, it can work on the contrary as the nucleation site of ferritic phase or pearlite phase, so that quenching degree is damaged, therefore Boron contents The upper limit is preferably limited to 0.01%.
Aluminium (Al)：Less than 0.1% (except 0%)
Aluminium (Al) is added for deoxidation and crystal grain miniaturization, and the content of aluminium is preferably limited to less than 0.1%, and (0% removes Outside).
In addition to foregoing element, surplus includes iron (Fe) and other inevitable impurity.
In the present invention, the minimum content of above-mentioned carbon (C) meets following relational expressions (1).
[relational expression 1]
C (minimum content of carbon (C)) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
(wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to hot rolling The value of cooling velocity when steel plate is cooled down, unit are DEG C/sec.)
Above-mentioned relation formula (1) is represented by the silicon (Si), manganese (Mn), chromium (Cr), molybdenum (Mo), nickel (Ni) and chromium (Cr) Composition obtains minimum carbon (C) content of the Brinell hardness of more than 500HB.
Even if the content of the carbon (C) meets 0.05~0.3 weight %, if can not meet the relational expression (1), nothing Method obtains the Brinell hardness of more than 500HB.
For example, the relational expression (1) can be designed using following relational expressions (3).
[relational expression 3]
HB (Brinell hardness)=100.4+830.5 × C+86.5 × Mn+28.8 × Si+73.4 × Cr+44.5 × Ni+28.8 ×Mo+0.252×C.R.
(wherein, C, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to heat The value of cooling velocity when rolled steel plate is cooled down, unit are DEG C/sec.)
The relational expression (1) of the minimum carbon content for HB >=500 of sening as an envoy to can be derived from the relational expression (3).
In addition, utilizing relational expression (3) in the steel plate composition range of the present invention, can also derive for obtaining HB350 The design condition of the appropriate alloying component of any necessary firmness level above.
The micro organization of the steel plate of the present invention includes the martensitic phase of more than 95 volume %.
When the martensitic phase is when dividing rate to be less than 95 volume %, it is difficult to ensure required intensity and hardness.
The micro organization of the steel plate of the present invention can include as the second phase constitution in addition to martensite and be less than 5.0 bodies One or both of ferrite and bainite of product %.
The steel plate of the present invention has the Brinell hardness of more than 500HB.
In the following, the manufacture method of the steel plate of the preferable other side of the present invention is illustrated.
In the manufacture method of the steel plate of the preferable other side of the present invention, heat is made by carrying out hot rolling to steel billet Cooled down after rolled steel plate, so as to manufacture the micro organization with the martensitic phase comprising more than 95 volume % and more than 500HB Brinell hardness steel plate, in terms of weight %, the steel billet is by carbon (C)：0.05~0.3%, silicon (Si)：Less than 0.5% (0% Except), manganese (Mn)：Less than 2.5% (except 0%), chromium (Cr)：Less than 1.5% (except 0%), molybdenum (Mo)：Less than 1.0% (except 0%), nickel (Ni)：Less than 1.0% (except 0%), niobium (Nb)：Less than 0.1% (except 0%), titanium (Ti)：0.1% with Under (except 0%), vanadium (V)：Less than 0.1% (except 0%), boron (B)：Less than 0.01% (except 0%), aluminium (Al)：0.1% with Under (except 0%), the iron (Fe) of surplus and other inevitable impurity compositions.
The minimum content of the carbon (C) of the steel billet meets following relational expressions (1).
[relational expression 1]
C (minimum content of carbon (C)) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
(wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to hot rolling The value of cooling velocity when steel plate is cooled down, unit are DEG C/sec.)
Before hot rolled steel plate is made to steel billet progress hot rolling, steel billet can be reheated.
The reheating condition of steel billet is not particularly limited, is homogenized then as long as realizing.
The relation reheating temperature of steel billet is preferably 1100~1300 DEG C.
The hot-rolled condition is not particularly limited, as long as the temperature that hot finishing temperature fully carries out austenitizing is then Can.
For example, the hot finishing temperature can be 870~930 DEG C, overall hot rolling can be after heating furnace taking-up 1150 DEG C to carrying out within the temperature range of hot finishing temperature.
For cooling velocity when the hot rolled steel plate cools down, as long as horses more than 95 volume % can be obtained The cooling velocity of family name's body phase, then be not particularly limited, for example, cooling velocity is more than 20 DEG C/sec, preferably 20~150 DEG C/ Second.
Cooling termination temperature when being cooled down to the hot rolled steel plate for Ms points (martensite start temperature) below, As long as the temperature of martensitic phases more than 95 volume % can be obtained, then it is not particularly limited.
Embodiment
In the following, more specific description is carried out to the present invention by embodiment.This embodiment is only used for illustrating the present invention, this It's not limited to that for invention.
(embodiment)
Use the composition (unit with table 1 below：Weight %) 17 kinds of steel of A to Q tested.
The composition of the steel of table 1 below is satisfied by the compositing range of the present invention.
The composition of steel of the manufacture with table 1 below and the steel plate that thickness is 30mm and width is 200mm, then at 1200 DEG C It is lower to reheat 180 minutes.Afterwards, under 900 DEG C of hot finishing temperature range, hot rolling, system are carried out to the steel plate by reheating The hot rolled steel plate that thickness is 3.0mm is made, is then cooled to 200 DEG C with the cooling velocity of table 2 below.
Brinell hardness (HB) and the micro organization of the hot rolled steel plate manufactured as described above are measured, and the results are shown in following In table 2.
Second phase constitution of table 2 below represents the second phase constitution in addition to martensite, the group in addition to the second phase It is woven to martensite, and 100% martensite is represented with 100% M.
In following second phase constitutions, F represents ferrite, and B represents bainite, and M represents martensite.
In addition, together shown in table 2 below by relational expression (1) calculate necessary carbon content, actual carbon content and The difference of actual carbon content and necessary carbon content.
[table 1]
[table 2]
As shown in Table 2 above, it is recognised that being more than the invention of necessary carbon content in actual carbon content according to the present invention In the case of example 1~9, Brinell hardness (HB) value is more than 500HB.
Furthermore it is possible to know, in the case where actual carbon content is less than the comparative example 1~9 of necessary carbon content, Bu Shi is hard Angle value is less than 500HB.
It is noted as above that the present invention is described, but in the concept and the situation of scope for not departing from claims Under, a variety of modifications and deformation can be carried out, this is easily to manage for general technical staff of the technical field of the invention Solution.

Claims (12)

1. high rigidity steel plate, its be by including the process cooled down to the hot rolled steel plate Jing Guo hot rolling come the steel plate that manufactures, In terms of weight %, the steel plate is by carbon (C)：0.05~0.3%, silicon (Si)：Except less than 0.5% and 0%, manganese (Mn)：2.5% Below and except 0%, chromium (Cr)：Except less than 1.5% and 0%, molybdenum (Mo)：Except less than 1.0% and 0%, nickel (Ni)： Except less than 1.0% and 0%, niobium (Nb)：Except less than 0.1% and 0%, titanium (Ti)：Except less than 0.1% and 0%, vanadium (V)： Except less than 0.1% and 0%, boron (B)：Except less than 0.01% and 0%, aluminium (Al)：Except less than 0.1% and 0%, surplus Iron (Fe) and other inevitable impurity compositions；
The minimum content of the carbon (C) meets following relational expressions (1)；
[relational expression 1]
The minimum content of carbon (C) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
Wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, C.R. be represent to hot rolled steel plate into The value of cooling velocity during row cooling, unit are DEG C/sec；
The steel plate has the micro organization of the martensitic phase comprising more than 95 volume %, and the Bu Shi with more than 500HB Hardness.
2. high rigidity steel plate according to claim 1, it is characterised in that the micro organization makees in addition to martensite One or both of ferrite and bainite less than 5.0 volume % is included for the second phase constitution.
3. high rigidity steel plate according to claim 1, it is characterised in that the relational expression (1) is by following relational expressions (3) Derive,
[relational expression 3]
Brinell hardness=100.4+830.5 × C+86.5 × Mn+28.8 × Si+73.4 × Cr+44.5 × Ni+28.8 × Mo+ 0.252×C.R.
Wherein, C, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, and C.R. is represented to hot rolled steel plate The value of cooling velocity when being cooled down, unit are DEG C/sec.
4. according to high rigidity steel plate according to any one of claims 1 to 3, it is characterised in that the content of the carbon (C) is 0.19~0.3%.
5. according to high rigidity steel plate according to any one of claims 1 to 3, it is characterised in that the content of the silicon (Si) is 0.21~0.5%.
6. according to high rigidity steel plate according to any one of claims 1 to 3, it is characterised in that the content of the manganese for 1.4~ 2.5%.
7. manufacture high rigidity steel plate method, the method be by steel billet carry out hot rolling and be made after hot rolled steel plate carry out it is cold But, so as to manufacture the steel with the micro organization of the martensitic phase comprising more than 95 volume % and the Brinell hardness of more than 500HB The method of plate, in terms of weight %, the steel billet is by carbon (C)：0.05~0.3%, silicon (Si)：Except less than 0.5% and 0%, manganese (Mn)：Except less than 2.5% and 0%, chromium (Cr)：Except less than 1.5% and 0%, molybdenum (Mo)：Except less than 1.0% and 0%, Nickel (Ni)：Except less than 1.0% and 0%, niobium (Nb)：Except less than 0.1% and 0%, titanium (Ti)：Less than 0.1% and 0% removes Outside, vanadium (V)：Except less than 0.1% and 0%, boron (B)：Except less than 0.01% and 0%, aluminium (Al)：Less than 0.1% and 0% removes Outside, the iron (Fe) of surplus and other inevitable impurity compositions；
The minimum content of the carbon (C) meets following relational expressions (1),
[relational expression 1]
The minimum content of carbon (C) >=
0.481-0.104Mn-0.035Si-0.088Cr-0.054Ni-0.035Mo-0.0003C.R.
Wherein, Mn, Si, Cr, Ni and Mo are the values for the content that each element is represented with weight %, C.R. be represent to hot rolled steel plate into The value of cooling velocity during row cooling, unit are DEG C/sec.
8. the method for manufacture high rigidity steel plate according to claim 7, it is characterised in that carried out to the hot rolled steel plate cold Cooling velocity when but is 20~150 DEG C/sec.
9. the method for the manufacture high rigidity steel plate according to claim 7 or 8, it is characterised in that to the hot rolled steel plate into Cooling termination temperature during row cooling is below Ms points, i.e., below martensite start temperature.
10. the method for the manufacture high rigidity steel plate according to claim 7 or 8, it is characterised in that the content of the carbon (C) For 0.19~0.3%.
11. the method for the manufacture high rigidity steel plate according to claim 7 or 8, it is characterised in that the content of the silicon (Si) For 0.21~0.5%.
12. the method for the manufacture high rigidity steel plate according to claim 7 or 8, it is characterised in that the content of the manganese is 1.4~2.5%.
CN201680047778.5A 2015-08-21 2016-08-18 High hardness steel sheet and method for producing same Active CN107923023B (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
KR1020150117985A KR101696094B1 (en) 2015-08-21 2015-08-21 Steel sheet having superior hardness and method for manufacturing the same
KR10-2015-0117985 2015-08-21
PCT/KR2016/009079 WO2017034216A1 (en) 2015-08-21 2016-08-18 High-hardness steel sheet, and manufacturing method therefor

Publications (2)

Publication Number Publication Date
CN107923023A true CN107923023A (en) 2018-04-17
CN107923023B CN107923023B (en) 2020-04-24

Family

ID=57835400

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201680047778.5A Active CN107923023B (en) 2015-08-21 2016-08-18 High hardness steel sheet and method for producing same

Country Status (6)

Country Link
US (1) US20180237875A1 (en)
EP (2) EP3339464B1 (en)
JP (1) JP6843119B2 (en)
KR (1) KR101696094B1 (en)
CN (1) CN107923023B (en)
WO (1) WO2017034216A1 (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112771194A (en) * 2018-09-27 2021-05-07 株式会社Posco Wear-resistant steel having excellent hardness and impact toughness and method for manufacturing same

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102031443B1 (en) 2017-12-22 2019-11-08 주식회사 포스코 Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same
KR102031446B1 (en) * 2017-12-22 2019-11-08 주식회사 포스코 Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same
KR102045646B1 (en) * 2017-12-26 2019-11-15 주식회사 포스코 Abrasion resistance steel having excellent homogeneous material properties and method for manufacturing the same
JP7163887B2 (en) * 2019-08-21 2022-11-01 Ｊｆｅスチール株式会社 Wear-resistant steel with excellent fatigue resistance
JP7163889B2 (en) * 2019-08-21 2022-11-01 Ｊｆｅスチール株式会社 Manufacturing method for wear-resistant steel with excellent fatigue resistance
DE102019215055A1 (en) * 2019-09-30 2021-04-01 Thyssenkrupp Steel Europe Ag Process for manufacturing a steel product and a corresponding steel product
CN113215488B (en) * 2021-05-07 2022-06-17 马鞍山钢铁股份有限公司 Heat-treatment-free NM360 wear-resistant steel plate and manufacturing method thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007277678A (en) * 2006-04-11 2007-10-25 Nippon Steel Corp High hardness hot rolled steel sheet having excellent weldability, workability and resistance to penetration by high speed impact and production method therefor
KR20120071614A (en) * 2010-12-23 2012-07-03 주식회사 포스코 Thick plate having excellent wear resistant and low-temperature toughness, and method for manufacturing the same
US20140090755A1 (en) * 2011-03-29 2014-04-03 Jfe Steel Corporation Abrasion resistant steel plate or steel sheet excellent in resistance to stress corrosion cracking and method for manufacturing the same
CN104508166A (en) * 2012-07-30 2015-04-08 杰富意钢铁株式会社 Abrasion-resistant steel plate and manufacturing process therefor
CN104685088A (en) * 2012-09-19 2015-06-03 杰富意钢铁株式会社 Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3425837B2 (en) * 1996-03-28 2003-07-14 株式会社神戸製鋼所 High-strength hot-rolled steel sheet, high-strength galvanized steel sheet excellent in pitting corrosion resistance and crushing properties, and methods for producing them
KR100536828B1 (en) * 1997-09-22 2006-02-28 카가쿠기쥬쯔죠 킨조쿠자이료 기쥬쯔켄큐죠 Grain steel based on fine-ferrite and method thereof
JP3736320B2 (en) * 2000-09-11 2006-01-18 Ｊｆｅスチール株式会社 Abrasion-resistant steel with excellent toughness and delayed fracture resistance and method for producing the same
WO2005106059A1 (en) * 2004-04-28 2005-11-10 Jfe Steel Corporation Parts for machine construction and method for production thereof
JP5423806B2 (en) * 2009-11-17 2014-02-19 新日鐵住金株式会社 High toughness wear resistant steel and method for producing the same
CN102517509A (en) * 2012-01-06 2012-06-27 江苏省沙钢钢铁研究院有限公司 HB500 (Brinell Hardness 500) wear-resistant steel plate and preparation method thereof
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

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007277678A (en) * 2006-04-11 2007-10-25 Nippon Steel Corp High hardness hot rolled steel sheet having excellent weldability, workability and resistance to penetration by high speed impact and production method therefor
KR20120071614A (en) * 2010-12-23 2012-07-03 주식회사 포스코 Thick plate having excellent wear resistant and low-temperature toughness, and method for manufacturing the same
US20140090755A1 (en) * 2011-03-29 2014-04-03 Jfe Steel Corporation Abrasion resistant steel plate or steel sheet excellent in resistance to stress corrosion cracking and method for manufacturing the same
CN104508166A (en) * 2012-07-30 2015-04-08 杰富意钢铁株式会社 Abrasion-resistant steel plate and manufacturing process therefor
CN104685088A (en) * 2012-09-19 2015-06-03 杰富意钢铁株式会社 Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112771194A (en) * 2018-09-27 2021-05-07 株式会社Posco Wear-resistant steel having excellent hardness and impact toughness and method for manufacturing same

Also Published As

Publication number Publication date
JP6843119B2 (en) 2021-03-17
EP4324954A3 (en) 2024-05-22
CN107923023B (en) 2020-04-24
EP3339464B1 (en) 2024-07-03
EP3339464A1 (en) 2018-06-27
US20180237875A1 (en) 2018-08-23
EP3339464A4 (en) 2018-08-08
JP2018528325A (en) 2018-09-27
KR101696094B1 (en) 2017-01-13
WO2017034216A1 (en) 2017-03-02
EP4324954A2 (en) 2024-02-21

Similar Documents

Publication Publication Date Title
CN107923023A (en) High rigidity steel plate and its manufacture method
CN110100034B (en) High-hardness wear-resistant steel and method for manufacturing same
US8852366B2 (en) Method for producing steel pipe with excellent expandability
CN103160736B (en) A kind of high strength bainite steel rail and thermal treatment process thereof
CN101889100B (en) High carbon steel sheet superior in tensile strength and elongation and method for manufacturing the same
JP5510025B2 (en) High strength thin steel sheet with excellent elongation and local ductility and method for producing the same
CN104870676B (en) Low yield ratio, high strength cold-rolled steel sheet and its manufacture method
JP7018510B2 (en) Wear-resistant steel with excellent hardness and impact toughness and its manufacturing method
CN104024452B (en) The super high tensile cold-rolled steel plate of weldability and excellent in bending workability and manufacture method thereof
CN103930585B (en) Thin steel sheet and process for producing same
CN108474083A (en) The non magnetic steel and its manufacturing method having superior hot workability
CN107109589A (en) The steel for high strength pressure vessel material and its manufacture method of tenacity excellent after PWHT
CN103361546A (en) Ultra-high strength strapping raw sheet and manufacturing method thereof
CN106498294A (en) A kind of high-level low-alloy wear-resistant steel of NM600 and its application
JP7368461B2 (en) Wear-resistant steel with excellent hardness and impact toughness and its manufacturing method
JP6803987B2 (en) High hardness wear resistant steel and its manufacturing method
CN103014545B (en) High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate
CN105543676A (en) Martensite-ferrite double-phase wear-resisting steel plate and preparing method thereof
CN105849295B (en) Weldability and the excellent hot rolled steel plate and preparation method thereof of deburring
CN105039861B (en) A kind of middle manganese boric low alloy wear resistant steel plate and preparation method thereof
US8652273B2 (en) High tensile steel for deep drawing and manufacturing method thereof and high-pressure container produced thereof
CN102021481A (en) Microalloyed bainite rail and thermal treatment method thereof
CN104745952A (en) Pressure vessel steel, manufacturing method thereof and manufacturing method of deep drawing article
CN109750222B (en) High-performance martensitic stainless steel and manufacturing method of high-flatness plate thereof
CN101586219A (en) Composite bainite steel product containing copper and method for producing the same

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
CP03 Change of name, title or address
CP03 Change of name, title or address

Address after: Seoul, South Kerean

Patentee after: POSCO Holdings Co.,Ltd.

Address before: Gyeongbuk, South Korea

Patentee before: POSCO

TR01 Transfer of patent right
TR01 Transfer of patent right

Effective date of registration: 20230613

Address after: Gyeongbuk, South Korea

Patentee after: POSCO Co.,Ltd.

Address before: Seoul, South Kerean

Patentee before: POSCO Holdings Co.,Ltd.