CN102959113A - Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance - Google Patents

Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance Download PDF

Info

Publication number
CN102959113A
CN102959113A CN2011800319242A CN201180031924A CN102959113A CN 102959113 A CN102959113 A CN 102959113A CN 2011800319242 A CN2011800319242 A CN 2011800319242A CN 201180031924 A CN201180031924 A CN 201180031924A CN 102959113 A CN102959113 A CN 102959113A
Authority
CN
China
Prior art keywords
steel plate
toughness
test
delayed fracture
wear
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.)
Pending
Application number
CN2011800319242A
Other languages
Chinese (zh)
Inventor
植田圭治
铃木伸一
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.)
JFE Steel Corp
JFE Engineering Corp
Original Assignee
NKK Corp
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 NKK Corp filed Critical NKK Corp
Publication of CN102959113A publication Critical patent/CN102959113A/en
Pending legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Provided is an abrasion-resistant steel plate or sheet which exhibits excellent weld toughness and excellent delayed fracture resistance and is thus suitable for construction machines, industrial machines, and so on. Specifically provided is a steel plate or sheet which contains, in mass%, 0.20 to 0.30% of C, 0.05 to 1.0% of Si, 0.40 to 1.2% of Mn, 0.010% or less of P, 0.005% or less of S, 0.40 to 1.5% of Cr, 0.005 to 0.025% of Nb, 0.005 to 0.03% of Ti, 0.1% or less of Al, 0.01% or less of N, and, as necessary, one or more of Mo, W, B, Cu, Ni, V, REM, Ca and Mg, and has a DI* of 45 to 180 while satisfying the relationship: C+Mn/4-Cr/3+10P<=0.47, and which has a microstructure that comprises martensite as the matrix phase. DI*=33.85(0.1C)0.5(0.7Si+1)(3.33Mn+1)(0.35Cu+1)(0.36Ni+1)(2.16Cr+1)(3Mo+1)(1.75V+1)(1.5W+1).

Description

The wear-resistant steel plate of the toughness of weld part and delayed fracture resistance characteristics excellence
Technical field
The present invention relates to the suitable wear-resistant steel plate (abrasionresistant steel plate or steel sheet) that supplies more than the thickness of slab 4mm of construction implement (construction machine), industrial machine (industrial machine), shipbuilding (ship buiding), steel pipe (steel pipe), building (civil engineering), building etc., particularly the excellent wear-resistant steel plate of the toughness of weld part (weldtoughness) and delayed fracture resistance characteristics (delayed fracture resistance).
Background technology
When in the iron structure thing of construction implement, industrial machine, shipbuilding, steel pipe, building, building etc. or machinery, device etc., using hot-rolled steel sheet, sometimes require the wearability (abrasionresistant property) of steel plate.In the past, as steel, in order to possess excellent wearability, usually improved hardness (hardness), and by forming martensite single phase structure (martensite singlephase microstructure), can improve by leaps and bounds hardness.In addition, in order to promote the hardness of martensitic stucture self, effectively increase solid solution C amount (amount of solid solutioncarbon).
Therefore, because the common cold crack susceptibility of wear-resistant steel plate (cold crackingsusceptibility) height, the poor toughness of weld part, so when being used for welded steel structure thing (weldedsteel structure), its surface that is fitted in the steel part that contacts with rock (rock), native sand (earth andsand) etc. is used as tectum (liner).For example, in the wagon box (vessel) of dump truck (damped motor lorry), sometimes use mild steel (mild steel) to assemble by weldprocedure after, only paste wear-resistant steel plate on the wagon box that contacts with native sand surface and utilize.
Yet the manufacture method of pasting wear-resistant steel plate behind the assembly welding works is made trouble, manufacturing cost increase, so a kind of wear-resistant steel plate that can be used as the use of welded structure strength member of demand.
Patent documentation 1 relates to wearability steel plate and the manufacture method thereof of delayed fracture resistance excellence, put down in writing and to have hanged down the low P-of Si-low S-Cr, Mo, Nb system in order to improve delayed fracture resistance characteristics and contain one or two or more kinds steel among Cu, V, Ti, B and the Ca in forming, direct quenching (direct quenching, be also referred to as DQ), carry out as required the technology of tempering (tempering).
Patent documentation 2 relates to the manufacture method of the high steel of wearability and steel work, put down in writing a kind of steel that improves wearability, it consists of at 0.24～0.3C-Ni, Cr, Mo, in the B system, the satisfied parameter type (parameter formula) that is formed by the content of these elements, and have martensite or the martensite bainite structure (martensitic structure and bainitic structure) of the austenite (austenite) that contains 5～15 volume %, and put down in writing the technology of between austenitizing temperature (austenitizing temperature)～450 ℃, cooling off the steel of this composition with the speed of cooling more than 1 ℃/second.
Patent documentation 3 relates to wear-resistant steel and the manufacture method thereof of toughness (toughness) and delayed fracture resistance excellence, a kind of steel have been put down in writing, it is with Cr that its one-tenth is grouped into, Ti, B is essential composition, the top layer is tempered martensite (tempered martensite), endoplasm section is tempered martensite and tempering lower bainite tissue (tempered lower bainitic structure), and, stipulated the ratio (aspect ratio of prioraustenite grain diameter) of wall thickness direction with the original austenite particle diameter of rolling direction, and, put down in writing the steel that this one-tenth is grouped into, below 900 ℃, after the condition of accumulation draft (cumulative reduction ratio) more than 50% carried out hot rolling, direct quenching, the technology of tempering.
Patent documentation 4 relates to wear-resistant steel and the manufacture method thereof of toughness and delayed fracture resistance excellence, a kind of steel have been put down in writing, it is with Cr that its one-tenth is grouped into, Ti, B is essential composition, the top layer is martensite, endoplasm section is mixed structure or the lower bainite single phase structure of martensite and lower bainite tissue, and stipulated the elongation (elongation rate) of the original austenite grain that represents with the ratio with respect to the rolling direction original austenite particle diameter of the original austenite particle diameter of thickness of slab central part, and put down in writing the steel that this one-tenth is grouped into, below 900 ℃, after the condition of accumulation draft more than 50% carried out hot rolling, the technology of direct quenching.
Patent documentation 5 relates to wearability and excellent Abrasion Resistant Steels and the manufacture method thereof of erosion resistance (corrosion resistance) of weldability (weldability), weld part, put down in writing a kind of steel, it is take the Cr of 4～9 quality % as essential element, contain a kind or 2 kinds among Cu, the Ni, the satisfied parameter type that is formed by the content of special component, and put down in writing the steel that this one-tenth is grouped into, below 950 ℃, after the accumulation condition of draft more than 30% carry out hot rolling, reheat with the temperature more than the Ac3, implement the technology of quench treatment.
Patent documentation 1: Japanese kokai publication hei 5-51691 communique
Patent documentation 2: Japanese kokai publication hei 8-295990 communique
Patent documentation 3: TOHKEMY 2002-115024 communique
Patent documentation 4: TOHKEMY 2002-80930 communique
Patent documentation 5: TOHKEMY 2004-162120 communique
Summary of the invention
Yet, when steel are carried out welded joint, the problem that toughness drop the most easily occurs is that the toughness in the fusion section (bond area) of welded bonds (fusion line) is deteriorated, and for the wear-resistant steel plate with martensitic stucture that keeps as-quenched condition, even if also be called as the deteriorated problem of toughness of low-temperaturetempering embrittlement (low-temperaturetempering embrittlement) on away from welding heat affected zone welded bonds, that reheat 300 ℃ of front and back (welded heat affected zone) (below, be also referred to as HAZ).Think that the low-temperaturetempering embrittlement is caused by the synergy of the grain boundary segregation (intergranular segregation) of the metamorphosis (morphology change) of the carbide in the martensite (carbide), impurity element etc.
Because the protection gas (shielding gas) during from welding etc. is immersed in the hydrogen of weld part with overlapping by the thermogenetic unrelieved stress of welding (residual stress); easily produce delayed fracture (this crackle that occurs at weld part is commonly called cold crack) so reheat the zone of low-temperaturetempering embrittlement temperature, delayed fracture particularly easily occurs in high-intensity wear-resistant steel plate.
Therefore, when wear-resistant steel plate is used for the welded structure strength member, need to improve fusion section and away from the toughness of the welding heat affected zone that reheats 300 ℃ of front and back of welded bonds, but the cold crack susceptibility of existing wear-resistant steel plate weld part is high, in order to prevent cold crack (cold crack), need to carry out in the front and back of welding the processing of preheating (preheating) or after heat (post heating) and so on, reduce release and the unrelieved stress of the hydrogen in the steel plate.
Do not put down in writing the toughness that improves the weld part in the Abrasion Resistant Steels in patent documentation 1 and 2, patent documentation 3 and 4 also is for the purpose of the toughness that improves mother metal, has stipulated microtexture.Although inquired into the wearability of weldability, weld part in the patent documentation 5, not that to improve toughness of welded zone be purpose, the Abrasion Resistant Steels that proposes in patent documentation 1～5 grade is unrealized toughness and the two improvement of delayed fracture resistance characteristics to weld part all.
Therefore, the object of the invention is to, under the prerequisite of the increase of the reduction that does not cause productivity and manufacturing cost, provide the wear-resistant steel plate of toughness and the delayed fracture resistance characteristics excellence of weld part.Toughness of welded zone means the toughness of welding heat affected zone in the present invention, and the toughness of welded zone excellence means particularly the tenacity excellent in fusion section and low-temperaturetempering embrittlement temperature zone.
The inventor etc. are in order to realize above-mentioned problem, take wear-resistant steel plate as object, in order to ensure toughness and the delayed fracture resistance characteristics of weld part, to the chemical composition of steel plate, manufacture method and determine that the various key elements of microtexture further investigate, obtained following opinion.
1. in order to ensure the wear-resistant property of excellence, the matrix that must make steel plate is martensite.Therefore, importantly the chemical constitution of stringent regulations steel plate is guaranteed hardening capacity.
2. in order to realize excellent toughness of welded zone, must be suppressed at the coarse grains of fusion section, for this reason, effectively in steel plate, disperse small precipitate, utilize pinning effect (pinningeffect).
3. in order to ensure the toughness in the excellence in the low-temperaturetempering embrittlement temperature zone of welding heat affected zone, suppress delayed fracture, the alloying element amount of importantly suitably managing C, Mn, Cr, P etc.
The present invention studies in a basic enterprising step of the opinion that obtains and finishes, that is, the present invention is as follows:
1. the wear-resistant steel plate of a toughness of welded zone and delayed fracture resistance characteristics excellence, has following composition: in quality %, contain C:0.20～0.30%, Si:0.05～1.0%, Mn:0.40～1.2%, below the P:0.010%, below the S:0.005%, Cr:0.40～1.5%, Nb:0.005～0.025%, Ti:0.005～0.03%, below the Al:0.1%, below the N:0.01%, hardenability index (hardenability index) DI* by formula (1) expression is more than 45, remainder is formed by Fe and inevitable impurity, and microtexture is as matrix phase take martensite.
DI＊＝33.85×（0.1×C） 0.5×（0.7×Si＋1）×（3.33×Mn＋1）×（0.35×Cu＋1）×（0.36×Ni＋1）×（2.16×Cr＋1）×（3×Mo＋1）×（1.75×V＋1）×（1.5×W＋1）·····（1）
In formula (1), each symbol of element is content (quality %).
2. as the wear-resistant steel plate of 1 described toughness of welded zone and delayed fracture resistance characteristics excellence, it is characterized in that, in above-mentioned steel forms, further contain one kind or two or more in Mo:0.05～1.0%, W:0.05～1.0%, B:0.0003～0.0030% in quality %.
3. as the wear-resistant steel plate of 1 or 2 described toughness of welded zone and delayed fracture resistance characteristics excellence, it is characterized in that, in above-mentioned steel forms, in quality % further contain below the Cu:1.5%, below the Ni:2.0%, V:0.1% is with lower one kind or two or more.
4. the wear-resistant steel plate of each described toughness of welded zone and delayed fracture resistance characteristics excellence as in 1～3, it is characterized in that, in above-mentioned steel forms, in quality % further contain below the REM:0.008%, below the Ca:0.005%, Mg:0.005% is with lower one kind or two or more.
5. the wear-resistant steel plate of each described toughness of welded zone and delayed fracture resistance characteristics excellence as in 1～4, the surface hardness of above-mentioned steel plate is counted more than the 400HBW10/3000 with Brinell hardness (Brinell hardness).
6. each described steel plate as in 1～5 is that hardenability index DI* is toughness of welded zone below 180 and the wear-resistant steel plate of delayed fracture resistance characteristics excellence.
As 1～6 in each described steel plate, be to satisfy the toughness of welded zone of formula (2) and the wear-resistant steel plate of delayed fracture resistance characteristics excellence.
C＋Mn/4－Cr/3＋10P≤0.47·····（2）
In formula (2), each symbol of element is content (quality %).
According to the present invention, obtain having the toughness of excellent weld part and the wear-resistant steel plate of delayed fracture resistance characteristics, help to improve manufacturing efficient, security when making steel structure, industrially play significant effect.
Description of drawings
Fig. 1 is the figure of the T-shaped Welding Crack test of explanation.
Fig. 2 is the collection position of the Charpy impact test sheet of weld part.
Embodiment
Predetermined component forms and microtexture in the present invention.
［ one-tenth is grouped into ］ in the following description % is quality %.
C：0.20～0.30%
C guarantees that for improving martensitic hardness excellent wearability is important element, in order to obtain this effect, must contain more than 0.20%.On the other hand, surpass 0.30% if contain, then not only weldability is deteriorated, and the toughness in fusion section and low-temperaturetempering zone is also deteriorated.Therefore, be limited to 0.20～0.30% scope.Be preferably 0.20～0.28%.
Si：0.05～1.0%
Si plays a role as reductor (deoxidizing agent), not only needs at steel processed, also has to be solid-solubilized in the effect that makes the steel plate high rigidity in the steel by solution strengthening (solid solution strengthening).And has the deteriorated effect of toughness in the temper embrittlement zone that suppresses welding heat affected zone.In order to obtain such effect, must contain more than 0.05%.On the other hand, surpass 1.0% if contain, then because the toughness of welding heat affected zone is significantly deteriorated, so be limited to 0.05～1.0% scope.Be preferably 0.07～0.5%.
Mn：0.40～1.2%
Mn has the effect of the hardening capacity (hardenability) that increases steel, is necessary for more than 0.40% in order to ensure the hardness of mother metal.On the other hand, surpass 1.2% if contain, then not only the toughness of mother metal, ductility and weldability are deteriorated, also encourage the grain boundary segregation of P, encourage the generation of delayed fracture.Therefore, be limited to 0.40～1.2% scope.Be preferably 0.40～1.1%.
Below the P:0.010%
Surpass 0.010% if contain P, then at grain boundary segregation, become the starting point that delayed fracture occurs, and make the toughness of welding heat affected zone deteriorated.Therefore, take 0.010% as the upper limit, preferably reduce as far as possible.Should illustrate, owing to exceedingly reducing P refining cost (refining cost) be gone up, unfavorable economically, so be preferably more than 0.002%.
Below the S:0.005%
Since S make mother metal low-temperature flexibility (low-temperature toughness), (ductility) is deteriorated for ductility, so preferably reduce take 0.005% as the upper limit.
Cr：0.40～1.5%
Cr is important alloying element in the present invention, has the effect of the hardening capacity that increases steel, and has the deteriorated effect of toughness in the temper embrittlement zone that suppresses welding heat affected zone.This is that when reheating the temperature province that produces the low-temperaturetempering embrittlement, the Carbide Morphology that suppresses in the martensite changes owing to by containing Cr, postponing the diffusion of C in steel plate.In order to have such effect, must contain more than 0.40%.On the other hand, surpass 1.5% if contain, then effect is saturated, and is unfavorable economically, and weldability reduces.Therefore, be limited to 0.40～1.5% scope.Be preferably 0.40～1.2%.
Nb：0.005～0.025%
Nb separates out as carbonitride (carbonitride), make the microtexture miniaturization of mother metal and welding heat affected zone, and be to have fixing solid solution N concurrently and improve the toughness of welding heat affected zone and suppress the important element of the effect that delayed fracture (delayed fracture) occurs.In order to obtain such effect, must contain more than 0.005%.On the other hand, surpass 0.025% if contain, thick Carbonitride Precipitation then becomes the starting point of fracture.Therefore, be limited to 0.005～0.025% scope.Be preferably 0.007～0.023%.
Ti：0.005～0.03%
Ti forms TiN by fixing solid solution N, thereby has the effect of thickization that suppresses the crystal grain in the fusion section, and has the effect that suppresses and delayed fracture generation deteriorated because of the toughness in the low tempering temperatures zone of solid solution N due to reducing.In order to obtain these effects, must contain more than 0.005%.On the other hand, surpass 0.03% if contain, then separate out TiC, base metal tenacity is deteriorated.Therefore, be limited to 0.005～0.03% scope.Be preferably 0.007～0.025%.
Below the Al:0.1%
Al plays a role as reductor, in the steel liquid deoxidation operation of steel plate, the most often uses.In addition, form AlN by the solid solution N in the fixing steel, have the effect that suppresses the coarse grains in the fusion section, and have the effect that toughness is deteriorated and delayed fracture occurs that suppresses because of in the low tempering temperatures zone of solid solution N due to reducing.On the other hand, surpass 0.1% if contain, then when welding, be blended into welding metal (weld metal), make the toughness of welding metal deteriorated, therefore be limited to below 0.1%.Be preferably 0.01～0.07%.
Below the N:0.01%
N has and Nb and Ti formation nitride (nitride), suppresses the effect of the coarse grains of welding heat affected zone.But, surpass 0.01% if contain, then mother metal and toughness of welded zone significantly descend, and therefore are defined as below 0.01%.Be preferably 0.0010 ~ 0.0070%.Remainder is Fe and inevitable impurity.
In the present invention, in order further to improve characteristic, can be on the basis of above-mentioned basal component system, contain one kind or two or more among Mo, W, B, Cu, Ni, V, REM, Ca, the Mg.
Mo：0.05～1.0%
Mo significantly increases hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, preferably be made as more than 0.05%.If surpass 1.0%, then base metal tenacity, ductility and anti-welding breaking caused negative impact, so be made as below 1.0%.
W：0.05～1.0%
W significantly increases hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, be preferably more than 0.05%, if but surpass 1.0%, then base metal tenacity, ductility and anti-welding breaking are caused negative impact, therefore be made as below 1.0%.
B：0.0003～0.0030%
B is that the interpolation of trace just can significantly increase hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, be preferably more than 0.0003%, if surpass 0.0030%, then base metal tenacity, ductility and anti-welding breaking (weld crack resistance) are caused negative impact, be below 0.0030% therefore.
Cu, Ni, V are the element of the intensity that helps to improve steel, can suitably contain according to desirable intensity.
Below the Cu:1.5%
Cu increases hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, be preferably more than 0.1%, but surpass 1.5%, then effect is saturated, produces red brittleness (hotbrittleness) and makes the surface texture of steel plate deteriorated, therefore is made as below 1.5%.
Below the Ni:2.0%
Ni increases hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, be preferably more than 0.1%, if surpass 2.0%, then effect is saturated, and is unfavorable economically, therefore is made as below 2.0%.
Below the V:0.1%
V increases hardening capacity, to the effective element of mother metal high rigidityization.In order to obtain such effect, be preferably more than 0.01%, but surpass 0.1%, then make base metal tenacity and deteriorated ductility, therefore be made as below 0.1%.
REM, Ca and Mg all help to improve toughness, can add according to desirable characteristic selectivity.When adding REM, be preferably more than 0.002%, even if but surpass 0.008%, effect also can be saturated, therefore take 0.008% as the upper limit.
When adding Ca, be preferably more than 0.0005%, even if but surpass 0.005%, effect also can be saturated, therefore take 0.005% as the upper limit.
When adding Mg, be preferably more than 0.001%, even if but surpass 0.005%, effect also can be saturated, therefore take 0.005% as the upper limit.
DI＊＝33.85×（0.1×C） 0.5×（0.7×Si＋1）×（3.33×Mn＋1）×（0.35×Cu＋1）×（0.36×Ni＋1）×（2.16×Cr＋1）×（3×Mo＋1）×（1.75×V＋1）×（1.5×W＋1）···（1）
Each symbol of element is content (quality %).
This parameter DI*(hardenability index) be that making the matrix of mother metal is martensite in the scope that mentioned component forms, make it have excellent wearability and the parameter stipulated, the value of this parameter is more than 45.Be lower than at 45 o'clock, less than 10mm, short as the Abrasion Resistant Steels life-span from the full hardening deepness on thickness of slab top layer.
If the value DI* of this parameter surpasses 180, then the matrix of mother metal is martensite, excelling in abrasion resistance, but the low-temperature flexibility of the cold crack during welding and weld part is deteriorated, therefore is preferably below 180.50～160 scope more preferably.
C＋Mn/4－Cr/3＋10P≤0.47···（2）
Each symbol of element is content (quality %).
So that the matrix of mother metal is martensite, make all have in the fusion section and low-temperaturetempering embrittlement region when carrying out weldprocedure excellent toughness become to be grouped into the time, need to be in the scope that mentioned component forms, make this parameter: the value of C+Mn/4-Cr/3+10P is below 0.47.Surpass at 0.47 o'clock, although the matrix of mother metal is martensite, excelling in abrasion resistance, the toughness of weld part is significantly deteriorated.Be preferably below 0.45.
［ microtexture ］
In the present invention, in order to improve wear-resistant property, the matrix phase (base phase or main phase) of the microtexture of steel plate is defined as martensite.Because the tissue of the bainite (bainite) beyond the martensite, ferrite (ferrite) etc. reduces wearability, so preferably do not mix as far as possible, if the total Area Ratio of these tissues (area ratio) is lower than 10%, then can ignore its impact.In addition, when the surface hardness of steel plate is lower than 400HBW10/3000 with Brinell tester, short as the Abrasion Resistant Steels life-span.Therefore, surface hardness is counted more than the 400HBW10/3000 with Brinell hardness.
In addition, the microtexture of fusion section is the mixed structure of martensite and bainite.Because the tissues such as the ferrite beyond martensite and the bainite reduce wearability, so preferably do not mix as far as possible, if the total Area Ratio of these tissues is lower than 20%, then can ignore its impact.
And in order to ensure the toughness of fusion section, median size is the following 1000/mm of existence of 1 μ m in the carbonitride of preferred Nb and Ti 2Above, the average crystallite particle diameter of original austenite is lower than 200 μ m and is that the average crystallite particle diameter of the undertissue (low microstructure) that surrounds of the high-angle boundary (large tiltgrain boundary) more than 15 ° is lower than 70 μ m by inclination angle (radial hook).
The Abrasion Resistant Steels that the present invention relates to can be made with following creating conditions.In explanation, with temperature correlation " ℃ " be illustrated in the temperature of 1/2 position of thickness of slab.Preferably use the molten steel of the above-mentioned composition of known melting method melting, utilize Continuous casting process (continuous castingprocess) or ingot formation method, make the steel material of the slab (slab) etc. of specified dimension.
Then, the steel material that obtains is heated to 950～1250 ℃ immediately without cooling ground after, perhaps behind cooling post-heating to 950～1250 ℃, carry out hot rolling, make the steel plate of desirable thickness of slab.Carry out immediately water-cooled after the hot rolling, perhaps reheat, quench.As required, be implemented in the tempering of 300 ℃ following conditions thereafter.
Embodiment 1
After being modulated into plate slab (steel slab) that the various one-tenth shown in the table 1 are grouped into and being heated to 1000～1250 ℃ with converter (steel converter)-ladle refining (ladle refining)-Continuous casting process, with the enforcement hot rolling of creating conditions shown in the table 2, after rolling to a part of steel plate enforcement, carry out immediately water-cooled ((DQ) quenches), cold in rolling laggard line space to another part steel plate, reheat after, carry out water-cooled (quench (RQ)).
The steel plate that obtains is implemented the toughness test of the weld part of surface hardness mensuration, wearability evaluation, base metal tenacity mensuration, T-shaped Welding Crack test (delayed fracture resistance characteristics evaluation), weld part reproduction thermal cycling test and actual joint by following main points.The obtained results are shown in table 3.
［ surface hardness 1 ］
Surface hardness is measured and is based on JIS Z2243(1998), measure the surface hardness (in the hardness of removing the surface of measuring after the oxide skin on top layer) under the top layer.Measure the tungsten hard sphere (tungsten hard ball) that uses diameter 10mm, load is 3000kgf.
［ base metal tenacity 1 ］
Based on JIS Z2202(1998) regulation, the direction vertical with rolling direction from thickness of slab 1/4 position of each steel plate, gather V notched specimen (V notch test specimen), based on JIS Z2242(1998) regulation each steel plate is implemented the Charpy impact test (Charpy impact test) of 3 test films of each temperature, obtain the absorption energy (absorbed energy) 0 ℃ of test temperature, estimate base metal tenacity.0 ℃ of test temperature is to consider in the use in warm area and selected.
The absorption energy of 0 ℃ of test temperature (is sometimes referred to as vE 0) the mean value of 3 test films be to be evaluated as base metal tenacity excellence (in the scope of the invention) more than the 30J.
［ wearability 1 ］
Wearability is based on the regulation of ASTM G65, implements rubber wheel test (rubber wheelabrasion test).Test film is 10mmt(t: thickness of slab) * and 75mmw(w: width) * 20mmL(L: length) (when thickness of slab is lower than 10mmt, the t(thickness of slab) * 75mmw * 20mmL), lost material uses 100%SiO 2Worn sand (abrasive sand) and implementing.
Test film weight before and after the determination test is measured abrasion loss.Test-results be abrasion loss take mild steel plate (SS400) as benchmark (1.0), with wear-resistant ratio: (abrasion loss of mild steel plate)/(abrasion loss of each steel plate) estimated.Wear-resistant ratio is larger, means that wearability is more excellent, in the scope of the invention, wear-resistant ratio is evaluated as excellent in wear resistance more than 4.0.
［ delayed fracture 1 ］
T-shaped Welding Crack test (T shape fillet weld cracking test) is after being assembled into as illustrated in fig. 1 T-shaped test body and implementing to restrain welding (restriction welding) with electrode arc welding (shielded metal arc welding), in room temperature (25 ℃ * humidity 60%) or after being preheating to 100 ℃, implement the test welding.
Welding process is as follows: (welding material: LB52UL(4.0mm Φ), heat is input as 17kJ/cm, implements the welding in 3 layer of 6 road with electrode arc welding.After the welding, after room temperature is placed 48 hours, gather 5 test board weld part cross-section samples (long 200mm carries out 5 five equilibriums to welding bead), observing by projector and optics microcosmic mirror (optical microscope) has flawless generation at welding heat affected zone.No matter being without preheating, still being preheating to 100 ℃, when each the 5 cross section sample that gathers, is that delayed fracture resistance characteristics is excellent at the average evaluation of the complete flawless generation of welding heat affected zone.
［ toughness of welded zone 1-1 ］
Welding reproduction thermal cycling test (synthetic heat-affected zone test) is fusion section and the low-temperaturetempering embrittlement region when simulating respectively the 1 layer of carbon dioxide arc welding that carries out welding heat input 17kJ/cm.The simulation of fusion section is to keep for 1 second at 1400 ℃, and the speed of cooling that makes 800～200 ℃ is 30 ℃/s.The simulation of low-temperaturetempering embrittlement region is to keep for 1 second at 300 ℃, makes 300～100 ℃ to cool off with 5 ℃/s.
After with high-frequency induction heating apparatus (high-frequency induction heating device) the square rod shape test film (square bar test specimen) that gathers from rolling direction being applied above-mentioned thermal cycling (heat cycle), based on JISZ2242(1998) carry out the Charpy impact test of V breach.The Charpy impact test of V breach is to carry out with 3 test films under 0 ℃ each steel plate in test temperature.
Absorption energy (vE with fusion section and low-temperaturetempering embrittlement region 0) the mean value of 3 test films separately be to be evaluated as toughness of welded zone excellence (in the scope of the invention) more than the 30J.
［ toughness of welded zone 1-2 ］
And, in order to confirm the toughness of actual joint, with electrode arc welding (shielded metal arcwelding) (heat input (heat input) 17kJ/cm, 150 ℃ of preheatings, welding material (weldingmaterial): LB52UL(4.0mm Φ)) steel plate is carried out built-up welding welding (bead on platewelding).The station acquisition Charpy impact test sheet of 1mm under the surface, with gap position as fusion section, based on JISZ2242(1998) carry out the Charpy impact test of V breach.The collection position of Charpy impact test sheet shown in Figure 2 and gap position (notch location).
The V breach Charpy impact test of actual joint (actual weld joint) be to each test temperature 0 ℃ of test temperature, carry out with 3 test films.Absorb energy (vE 0) the mean value of 3 test films be to be evaluated as fusion section tenacity excellent (in the scope of the invention) more than the 30J.
Creating conditions of the steel plate of testing shown in the table 2, in the result of above-mentioned each test shown in the table 3.Can confirm that surface hardness is more than the 400HBW10/3000 in the inventive example (steel No.1～5), excellent in wear resistance, 0 ℃ base metal tenacity is more than the 30J, and in T-shaped Welding Crack test crackle does not occur, in addition, reproduce the toughness that all has excellence in thermal cycling test and the actual welding section at weld part, toughness of welded zone is excellent.
On the other hand, can confirm into that one or more in surface hardness, wearability, T-shaped Welding Crack test, base metal tenacity, reproduction thermal cycling Charpy impact test, the actual joint Charpy impact test (Charpy impact test of actualweld joint) can't satisfy target capabilities in the comparative example (No.6～14) that is grouped into outside the scope of the invention.
Embodiment 2
After being modulated into plate slab that the various one-tenth shown in the table 4 are grouped into and being heated to 1000～1250 ℃ with converter-ladle refining-Continuous casting process, with the enforcement hot rolling of creating conditions shown in the table 5, after rolling to a part of steel plate enforcement, carry out immediately water-cooled ((DQ) quenches), cold in rolling laggard line space to another part steel plate, after reheating, carry out water-cooled ((RQ) quenches).
The steel plate that obtains is implemented the toughness test of the weld part of surface hardness mensuration, wearability evaluation, base metal tenacity mensuration, T-shaped Welding Crack test (delayed fracture resistance characteristics evaluation), weld part reproduction thermal cycling test and actual joint by following main points.The obtained results are shown in table 6.
［ surface hardness 2 ］
Surface hardness is measured and is based on JIS Z2243(1998), measure the surface hardness (in the hardness of removing the surface of measuring after the oxide skin on top layer) under the top layer.Measure the tungsten hard sphere that uses diameter 10mm, load is 3000kgf.
［ base metal tenacity 2 ］
Based on JIS Z2202(1998) regulation, the direction vertical with rolling direction from thickness of slab 1/4 position of each steel plate, gather the V notched specimen, based on JIS Z2242(1998) regulation each steel plate is implemented the Charpy impact test of 3 test films of each temperature, obtain at 0 ℃ of test temperature and-40 ℃ of lower absorption energy, evaluation base metal tenacity.0 ℃ of test temperature is the use of considering in warm area, and test temperature-40 ℃ is to consider in the use of cold district (cold region) and selected.
The absorption energy of 0 ℃ of test temperature (is sometimes referred to as vE 0) the mean value of 3 test films be that the absorption energy of the above and test temperature-40 of 30J ℃ (is sometimes referred to as vE- 40) the mean value of 3 test films be to be evaluated as base metal tenacity excellence (in the scope of the invention) more than the 27J.Should illustrate, be lower than the steel plate of 10mm for thickness of slab, (the V breach Charpy test sheet of 5mm * 10mm) is implemented Charpy impact test, will absorb energy (vE to gather small size 0) the mean value of 3 test films be that 15J is above and absorb energy (vE- 40) the mean value of 3 test films be to be evaluated as base metal tenacity excellence (in the scope of the invention) more than the 13J.
［ wearability 2 ］
Wearability is based on the regulation of ASTM G65, implements the rubber wheel test.Test film is 10mmt(t: thickness of slab) * and 75mmw(w: width) * 20mmL(L: length) (when thickness of slab is lower than 10mmt, the t(thickness of slab) * 75mmw * 20mmL), lost material uses 100%SiO 2Worn sand and implementing.
Test film weight before and after the determination test is measured abrasion loss.Test-results be abrasion loss take mild steel plate (SS400) as benchmark (1.0), with wear-resistant ratio: (abrasion loss of mild steel plate)/(abrasion loss of each steel plate) estimated.Wear-resistant ratio is larger, means that wearability is more excellent, in the scope of the invention, wear-resistant ratio is evaluated as excellent in wear resistance more than 4.0.
［ delayed fracture 2 ］
The test of T-shaped Welding Crack is after being assembled into as illustrated in fig. 1 T-shaped test body and implementing to restrain welding with electrode arc welding, in room temperature (25 ℃ * humidity 60%) or after being preheating to 100 ℃, to implement the test welding.
Welding process is as follows: (welding material: LB52UL(4.0mm Φ), heat is input as 17kJ/cm, implements the welding in 3 layer of 6 road with electrode arc welding.After the test, after room temperature is placed 48 hours, gather 5 test board weld part cross-section samples (long 200mm carries out 5 five equilibriums to welding bead), at welding heat affected zone flawless generation is arranged by projector and optics microcosmic sem observation.No matter being without preheating, still being preheating to 100 ℃, in each the 5 cross section sample that gathers, is that delayed fracture resistance characteristics is excellent at the average evaluation of the complete flawless generation of welding heat affected zone.
［ toughness of welded zone 2-1 ］
It is to simulate respectively 1 layer of carbon dioxide arc welding (the one pass CO that carries out welding heat input 17kJ/cm that thermal cycling test is reproduced in welding 2Gas shielded arc welding) fusion section and low-temperaturetempering embrittlement region the time.The simulation of fusion section is to keep for 1 second at 1400 ℃, and the speed of cooling that makes 800～200 ℃ is 30 ℃/s.In addition, the simulation of low-temperaturetempering embrittlement region is to keep for 1 second at 300 ℃, makes 300～100 ℃ to cool off with 5 ℃/s.
After with high-frequency induction heating apparatus the square rod shape test film from the rolling direction collection being applied above-mentioned thermal cycling, based on JISZ2242(1998) carry out the Charpy impact test of V breach.The Charpy impact test of V breach is carried out with 3 test films of each temperature each steel plate under 0 ℃ of test temperature and-40 ℃.
Absorption energy (vE with fusion section and low-temperaturetempering embrittlement region 0) the mean value of 3 test films separately be that 30J is above and absorb energy (vE -40) the mean value of 3 test films separately be that the above average evaluation of 27J is toughness of welded zone excellent (in the scope of the invention).
Should illustrate, be lower than the steel plate of 10mm for thickness of slab, (the V breach Charpy test sheet of 5mm * 10mm) is implemented Charpy impact test, with the absorption energy (vE of fusion section and low-temperaturetempering embrittlement region to gather small size 0) the mean value of 3 test films separately be that 15J is above and absorb energy (vE -40) the mean value of 3 test films separately be that the above average evaluation of 13J is toughness of welded zone excellent (in the scope of the invention).
［ toughness of welded zone 2-2 ］
And, in order further to confirm the toughness of actual joint, with electrode arc welding (heat input 17kJ/cm, 150 ℃ of preheatings, welding material: LB52UL(4.0mm Φ)) steel plate is carried out the built-up welding welding.The station acquisition Charpy impact test sheet of 1mm under the surface, with gap position as fusion section, based on JISZ2242(1998) carry out the Charpy impact test of V breach.The collection position of Charpy impact test sheet shown in Figure 2 and gap position.
The V breach Charpy impact test of actual joint is 0 ℃ of test temperature and-40 ℃, carries out with 3 test films of each test temperature.Absorb energy (vE 0) the mean value of 3 test films be that 30J is above and absorb energy (vE -40) the mean value of 3 test films be that the above average evaluation of 27J is the tenacity excellent (in the scope of the invention) of fusion section.
Should illustrate, be lower than the steel plate of 10mm for thickness of slab, (the V breach Charpy test sheet of 5mm * 10mm) is implemented Charpy impact test, absorbs energy (vE to gather small size 0) the mean value of 3 test films be that 15J is above and absorb energy (vE -40) the mean value of 3 test films be that the above average evaluation of 13J is fusion section tenacity excellent (in the scope of the invention).
Creating conditions of the steel plate of testing shown in the table 5, in the result of above-mentioned each test shown in the table 6.(steel No.15～17(wherein can to confirm the inventive example, No.17 is thickness of slab 8mm)) in surface hardness be more than the 400HBW10/3000, excellent in wear resistance, 0 ℃ base metal tenacity is that 30J base metal tenacity above and-40 ℃ is more than the 27J, and in T-shaped Welding Crack test crackle does not occur, in addition, reproduce the toughness that excellence is all arranged in thermal cycling test and the actual welding section at weld part, toughness of welded zone is excellent.
On the other hand, become to be grouped within the scope of the present invention, but DI* surpasses among 180 the steel No.18, surface hardness, wearability, base metal tenacity and the test of T-shaped Welding Crack are good, but near the lower value of target capabilities, the low-temperature flexibility of weld part is compared relatively poor with other example in the reproduction thermal cycling Charpy impact test that is equivalent to the low-temperaturetempering embrittlement region and actual joint Charpy impact test.
For steel No.19, in becoming to be grouped into, Si is outside the scope of the invention, although therefore surface hardness, wearability, base metal tenacity are well, but the poor toughness in the temper embrittlement zone of welding heat affected zone can't satisfy target capabilities in T-shaped Welding Crack test, the reproduction thermal cycling Charpy impact test that is equivalent to the low-temperaturetempering embrittlement region and actual joint Charpy impact test.
Become to be grouped within the scope of the present invention among the steel No.20, but formula (2) surpasses 0.47, so reproduce thermal cycling Charpy impact test, actual joint Charpy impact test and vE -40Near the lower limit of performance of the present invention, compare relatively poor with other example.In addition, steel No.18, the 20th in table 4,5,6 record becomes to be grouped in the scope of technical solution of the present invention 3, but the value of DI*, formula (2) is outside technical solution of the present invention 6,7 scope, therefore with it as a comparative example.
Figure BDA00002662092800181
Table 2
Figure BDA00002662092800191
Annotate 1: underscore is outside the scope of the invention
Figure BDA00002662092800201
Figure BDA00002662092800211
Table 5
Figure BDA00002662092800221
Annotate: underscore is outside the scope of the invention
Figure BDA00002662092800231

Claims (7)

1. the wear-resistant steel plate of a toughness of welded zone and delayed fracture resistance characteristics excellence has following composition:
In quality %, contain that C:0.20～0.30%, Si:0.05～1.0%, Mn:0.40～1.2%, P:0.010% are following, S:0.005% is following, Cr:0.40～1.5%, Nb:0.005～0.025%, Ti:0.005～0.03%, Al:0.1% are following, below the N:0.01%, hardenability index DI* by formula (1) expression is more than 45, remainder is formed by Fe and inevitable impurity, and microtexture is as matrix phase take martensite;
DI＊＝33.85×（0.1×C） 0.5×（0.7×Si＋1）×（3.33×Mn＋1）×（0.35×Cu＋1）×（0.36×Ni＋1）×（2.16×Cr＋1）×（3×Mo＋1）×（1.75×V＋1）×（1.5×W＋1）·····（1）
In the formula (1), each symbol of element is the content in quality %.
2. the wear-resistant steel plate of toughness of welded zone according to claim 1 and delayed fracture resistance characteristics excellence, it is characterized in that, in described steel forms, further contain one kind or two or more in Mo:0.05～1.0%, W:0.05～1.0%, B:0.0003～0.0030% in quality %.
3. the wear-resistant steel plate of toughness of welded zone according to claim 1 and 2 and delayed fracture resistance characteristics excellence, it is characterized in that, in described steel forms, in quality % further contain below the Cu:1.5%, below the Ni:2.0%, V:0.1% is with lower one kind or two or more.
4. the wear-resistant steel plate of each described toughness of welded zone and delayed fracture resistance characteristics excellence according to claim 1～3, it is characterized in that, in described steel forms, in quality % further contain below the REM:0.008%, below the Ca:0.005%, Mg:0.005% is with lower one kind or two or more.
5. the wear-resistant steel plate of each described toughness of welded zone and delayed fracture resistance characteristics excellence according to claim 1～4, the surface hardness of described steel plate is counted more than the 400HBW10/3000 with Brinell hardness.
6. each described steel plate according to claim 1～5 is that hardenability index DI* is toughness of welded zone below 180 and the wear-resistant steel plate of delayed fracture resistance characteristics excellence.
7. each described steel plate according to claim 1～6 is to satisfy the toughness of welded zone of formula (2) and the wear-resistant steel plate of delayed fracture resistance characteristics excellence;
C＋Mn/4–Cr/3＋10P≤0.47·····（2）
In the formula (2), each symbol of element is the content in quality %.
CN2011800319242A 2010-06-30 2011-06-29 Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance Pending CN102959113A (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP2010149649 2010-06-30
JP2010-149649 2010-06-30
JP2011142506A JP5866820B2 (en) 2010-06-30 2011-06-28 Wear-resistant steel plate with excellent weld toughness and delayed fracture resistance
JP2011-142506 2011-06-28
PCT/JP2011/065416 WO2012002567A1 (en) 2010-06-30 2011-06-29 Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance

Publications (1)

Publication Number Publication Date
CN102959113A true CN102959113A (en) 2013-03-06

Family

ID=45402264

Family Applications (1)

Application Number Title Priority Date Filing Date
CN2011800319242A Pending CN102959113A (en) 2010-06-30 2011-06-29 Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance

Country Status (10)

Country Link
US (1) US20130216422A1 (en)
EP (1) EP2589676B1 (en)
JP (1) JP5866820B2 (en)
KR (1) KR20130045900A (en)
CN (1) CN102959113A (en)
AU (1) AU2011272188C1 (en)
CA (1) CA2801703C (en)
MX (1) MX354630B (en)
RU (1) RU2550985C2 (en)
WO (1) WO2012002567A1 (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103225046A (en) * 2013-04-09 2013-07-31 康力电梯股份有限公司 Alloy member with high comprehensive performance
CN104711480A (en) * 2015-03-20 2015-06-17 苏州科胜仓储物流设备有限公司 Dedicated wear-resisting anticorrosion steel plate for storage rack platform and preparation method of steel plate
CN105189803A (en) * 2013-03-28 2015-12-23 杰富意钢铁株式会社 Abrasion resistant steel plate having low-temperature toughness and hydrogen embrittlement resistance, and manufacturing method therefor

Families Citing this family (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
MX341765B (en) * 2011-03-29 2016-09-02 Jfe Steel Corp Abrasion-resistant steel sheet exhibiting excellent resistance to stress corrosion cracking, and method for producing same.
CN103459635B (en) * 2011-03-29 2016-08-24 杰富意钢铁株式会社 The wear-resistant steel plate of anticorrosion stress-resistant cracking behavior excellence and manufacture method thereof
JP5966730B2 (en) 2012-07-30 2016-08-10 Ｊｆｅスチール株式会社 Abrasion resistant steel plate with excellent impact wear resistance and method for producing the same
CN102876969B (en) * 2012-07-31 2015-03-04 宝山钢铁股份有限公司 Super-strength high-toughness wear resistant steel plate and production method thereof
CN102747280B (en) * 2012-07-31 2014-10-01 宝山钢铁股份有限公司 Wear resistant steel plate with high intensity and high toughness and production method thereof
CN102747282B (en) 2012-07-31 2015-04-22 宝山钢铁股份有限公司 High-hardness high-tenacity wear-resistant steel plate and production method thereof
EP2873748B1 (en) * 2012-09-19 2018-03-14 JFE Steel Corporation Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance
PE20150779A1 (en) 2012-09-19 2015-05-30 Jfe Steel Corp ABRASION RESISTANT STEEL PLATE THAT HAS EXCELLENT HARDNESS AT LOW TEMPERATURES AND EXCELLENT RESISTANCE TO CORROSION WEAR
CN103966524B (en) * 2013-01-24 2016-11-02 中国石油天然气集团公司 A kind of tubing and casing of resistance against sulfide stress cracking
CN103205634B (en) * 2013-03-28 2016-06-01 宝山钢铁股份有限公司 A kind of low-alloy high hardness wear-resisting steel plate and manufacture method thereof
EP2789699B1 (en) * 2013-08-30 2016-12-28 Rautaruukki Oy A high-hardness hot-rolled steel product, and a method of manufacturing the same
MX2016009700A (en) * 2014-01-28 2016-09-22 Jfe Steel Corp Wear-resistant steel plate and process for producing same.
CN103952645B (en) * 2014-04-10 2016-10-05 铜陵南江鑫钢实业有限公司 A kind of high temperature resistant wear-resistance high-manganese steel and preparation method thereof
JP6217585B2 (en) * 2014-10-20 2017-10-25 Ｊｆｅスチール株式会社 Abrasion resistant steel plate excellent in bending workability and impact wear resistance and method for producing the same
CN108251761A (en) * 2018-02-26 2018-07-06 朱威威 Rare-earth and high chromium tungsten high temperature resistant and wear-resistant steel
WO2021054015A1 (en) * 2019-09-17 2021-03-25 Ｊｆｅスチール株式会社 Wear-resistant steel sheet and method for producing same
CN111304546A (en) * 2020-04-07 2020-06-19 四川泰铸耐磨材料有限公司 Super-strength wear-resistant alloy and preparation method thereof
KR102498142B1 (en) * 2020-12-18 2023-02-08 주식회사 포스코 Armored steel havinh high hardness and excellent low-temperature impact toughness and method for manufacturing thereof
CN113512688B (en) * 2021-07-15 2022-04-26 重庆增隆新材料科技有限公司 Spherical powder material for aviation ultrahigh-strength steel and preparation method thereof

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007070713A (en) * 2005-09-09 2007-03-22 Nippon Steel Corp High toughness wear resistant steel small in hardness change during using, and producing method therefor
JP2009030094A (en) * 2007-07-26 2009-02-12 Jfe Steel Kk Wear resistant steel sheet excellent in gas cut face property and low temperature tempering brittle crack resistance
JP2009030092A (en) * 2007-07-26 2009-02-12 Jfe Steel Kk Wear resistant steel sheet excellent in low temperature toughness and low temperature tempering brittle crack resistance

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0551691A (en) 1991-03-11 1993-03-02 Sumitomo Metal Ind Ltd Wear resistant steel sheet excellent in delayed fracture resistance and its production
FR2733516B1 (en) 1995-04-27 1997-05-30 Creusot Loire STEEL AND PROCESS FOR THE MANUFACTURE OF PARTS WITH HIGH ABRASION RESISTANCE
JP3543619B2 (en) * 1997-06-26 2004-07-14 住友金属工業株式会社 High toughness wear-resistant steel and method of manufacturing the same
JPH11201168A (en) * 1998-01-12 1999-07-27 Nippon Seiko Kk Rolling bearing
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
JP2002115024A (en) 2000-10-06 2002-04-19 Nkk Corp Wear resistant steel having excellent toughness and delayed-fracture resistance and its production method
JP4116867B2 (en) 2002-11-13 2008-07-09 新日本製鐵株式会社 Abrasion resistant steel with excellent weldability and wear resistance and corrosion resistance of welded parts, and method for producing the same
FR2847272B1 (en) * 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET
RU2243288C1 (en) * 2003-12-03 2004-12-27 Открытое акционерное общество "Северсталь" Steel
JP2008214651A (en) * 2007-02-28 2008-09-18 Jfe Steel Kk Wear resistant steel sheet having excellent weldability
JP5145804B2 (en) * 2007-07-26 2013-02-20 Ｊｆｅスチール株式会社 Abrasion-resistant steel plate with excellent low-temperature tempering embrittlement cracking properties
JP2012031511A (en) * 2010-06-30 2012-02-16 Jfe Steel Corp Wear-resistant steel sheet having excellent toughness of multi-layer-welded part and lagging destruction resistance properties
CN103459635B (en) * 2011-03-29 2016-08-24 杰富意钢铁株式会社 The wear-resistant steel plate of anticorrosion stress-resistant cracking behavior excellence and manufacture method thereof
MX341765B (en) * 2011-03-29 2016-09-02 Jfe Steel Corp Abrasion-resistant steel sheet exhibiting excellent resistance to stress corrosion cracking, and method for producing same.

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007070713A (en) * 2005-09-09 2007-03-22 Nippon Steel Corp High toughness wear resistant steel small in hardness change during using, and producing method therefor
JP2009030094A (en) * 2007-07-26 2009-02-12 Jfe Steel Kk Wear resistant steel sheet excellent in gas cut face property and low temperature tempering brittle crack resistance
JP2009030092A (en) * 2007-07-26 2009-02-12 Jfe Steel Kk Wear resistant steel sheet excellent in low temperature toughness and low temperature tempering brittle crack resistance

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105189803A (en) * 2013-03-28 2015-12-23 杰富意钢铁株式会社 Abrasion resistant steel plate having low-temperature toughness and hydrogen embrittlement resistance, and manufacturing method therefor
CN105189803B (en) * 2013-03-28 2018-05-04 杰富意钢铁株式会社 Wear-resisting steel plate and its manufacture method with low-temperature flexibility and resistance to hydrogen embrittlement
US10253385B2 (en) 2013-03-28 2019-04-09 Jfe Steel Corporation Abrasion resistant steel plate having excellent low-temperature toughness and hydrogen embrittlement resistance and method for manufacturing the same
CN103225046A (en) * 2013-04-09 2013-07-31 康力电梯股份有限公司 Alloy member with high comprehensive performance
CN104711480A (en) * 2015-03-20 2015-06-17 苏州科胜仓储物流设备有限公司 Dedicated wear-resisting anticorrosion steel plate for storage rack platform and preparation method of steel plate

Also Published As

Publication number Publication date
EP2589676A4 (en) 2017-04-19
MX354630B (en) 2018-03-14
JP2012031510A (en) 2012-02-16
CA2801703A1 (en) 2012-01-05
EP2589676B1 (en) 2020-04-22
EP2589676A1 (en) 2013-05-08
KR20130045900A (en) 2013-05-06
WO2012002567A1 (en) 2012-01-05
JP5866820B2 (en) 2016-02-24
RU2013103814A (en) 2014-08-10
US20130216422A1 (en) 2013-08-22
MX2013000031A (en) 2013-02-01
AU2011272188B2 (en) 2014-05-01
CA2801703C (en) 2016-05-24
RU2550985C2 (en) 2015-05-20
AU2011272188C1 (en) 2014-12-04

Similar Documents

Publication Publication Date Title
CN102959113A (en) Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance
CN102959112A (en) Wear-resistant steel sheet having excellent welded part toughness and lagging destruction resistance properties
KR101846759B1 (en) Steel plate and method for manufacturing same
US10023946B2 (en) Thick steel sheet having excellent CTOD properties in multilayer welded joints, and manufacturing method for thick steel sheet
CN103459635A (en) Abrasion-resistant steel sheet exhibiting excellent resistance to stress corrosion cracking, and method for producing same
US8048367B2 (en) High strength thick-gauge steel plate superior in weldability and having tensile strength of 780 MPA or more and method of production of same
JP2007119850A (en) Wear resistant steel plate with excellent low-temperature toughness, and method for manufacturing the same
JP5708431B2 (en) Steel sheet excellent in toughness of weld heat-affected zone and method for producing the same
JP7226598B2 (en) Abrasion-resistant steel plate and manufacturing method thereof
JP5849940B2 (en) Low yield ratio high strength steel plate with excellent weld heat affected zone toughness
EP3128024B1 (en) Welded joint
JP4344919B2 (en) High strength steel plate excellent in weldability without preheating, its manufacturing method and welded steel structure
JP2019173053A (en) High strength high ductility steel sheet
JP2002161330A (en) Wear resistant steel
JP2007224404A (en) High tensile strength steel plate having excellent strength and low temperature toughness, and method for producing high tensile strength steel plate
JP5862592B2 (en) High-tensile steel plate with excellent weld heat-affected zone toughness
JPH10158778A (en) High tensile strength steel plate excellent in toughness and weldability, and its production
JP7205618B2 (en) steel
JP2002030380A (en) High tensile strength steel excellent in welded joint toughness and its production method
JP2016164289A (en) High tensile steel for weldment
KR20120014413A (en) High strength steel plate for welding structure with superior haz toughness for high heat input welding and method for manufacturing the same
JP2006257490A (en) Steel for welded structure having excellent weld zone ctod property

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
RJ01 Rejection of invention patent application after publication
RJ01 Rejection of invention patent application after publication

Application publication date: 20130306