CN102959112A - Wear-resistant steel sheet having excellent welded part toughness and lagging destruction resistance properties - Google Patents

Wear-resistant steel sheet having excellent welded part toughness and lagging destruction resistance properties Download PDF

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CN102959112A
CN102959112A CN2011800319079A CN201180031907A CN102959112A CN 102959112 A CN102959112 A CN 102959112A CN 2011800319079 A CN2011800319079 A CN 2011800319079A CN 201180031907 A CN201180031907 A CN 201180031907A CN 102959112 A CN102959112 A CN 102959112A
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steel plate
toughness
welding
test
wear
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植田圭治
铃木伸一
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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Abstract

Disclosed is a wear-resistant steel sheet which has excellent toughness of a multi-layer-welded part and excellent lagging destruction resistance properties and is therefore suitable for a construction machine, an industrial machine and the like. Specifically disclosed is a steel sheet which contains, in mass%, 0.20-0.30% of C, 0.05-1.0% of Si, 0.40-1.2% of Mn, 0.010% or less of P, 0.005% or less of S, 0.40-1.5% of Cr, 0.005-0.025% of Nb, 0.05-1.0% of Mo, 0.005-0.03% of Ti, 0.1% or less of Al, 0.01% or less of N and 0.0003-0.0020% of B, optionally contains at least one element selected from W, Cu, Ni, V, REM, Ca and Mg, and fulfils the requirements represented by the following formulae: 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)): 45-180 and C+Mn/4-Cr/3+10P <= 0.47, wherein the microstructure of the steel sheet contains martensite as the matrix phase.

Description

The wear-resistant steel plate of toughness of welded zone and delayed fracture resistance characteristics excellence
Technical field
The present invention relates to be fit to supply in construction implement (construction machine), industrial machine (industrial machine), shipbuilding (ship buiding), steel pipe (steel pipe), building (civil engineering), the wear-resistant steel plate (abrasionresistant steel plate or steel sheet) that the thickness of slab 4mm of building etc. is above, the particularly excellent wear-resistant steel plate of the toughness (toughness) of multi-run welding weld part (malti passweld) and delayed fracture resistance characteristics (delayed fractureresistance).
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 to assemble by weldprocedure after, only paste wear-resistant steel plate on the wagon box that contacts with native sand surface and utilize.
Yet, paste the manufacture method of wear-resistant steel plate behind the assembly welding works, make trouble, manufacturing cost increase, can be used as the wear-resistant steel plate of that the welded structure strength member uses, weldability, toughness of welded zone excellence so demand is a kind of, the wear-resistant steel plate of patent documentation 1～5 has for example been proposed thus.
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, its composition is 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, for the welding joint that thickness of slab is the steel plate more than the 4mm, the normal multi-run welding (malti pass welding) that adopts, on weld part, the fusion section of welding bead formerly (bond area) is reheated by follow-up welding, significantly deteriorated zone of toughness appears, particularly, for wear-resistant steel plate, the fusion section of the welding in the 1st road is reheated in the situation of 300 ℃ of front and back by follow-up welding, because low-temperaturetempering embrittlement (low-temperature temperingembrittlement), toughness is significantly deteriorated.
Think that the low-temperaturetempering embrittlement is that synergy by the grain boundary segregation (intergranularsegregation) of the metamorphosis (morphology change) of the carbide in the martensite (carbide) and impurity element etc. is caused, at coarse grains and the fusion section of containing in a large number solid solution N become particularly remarkable.Pointed out on such zone that reheats the low-temperaturetempering embrittlement temperature, easily to produce delayed fracture.
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 all is for the purpose of the toughness that improves mother metal, has stipulated microtexture.Although patent documentation 5 has been inquired into the wearability of weldability, weld part, but be 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 the multi-run welding 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 multi-run welding weld part.
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 multi-run welding 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 (basemicrostructure or main microstructure) (being also referred to as matrix phase (base phase ormain phase)) 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 the toughness of excellent multi-run welding weld part, the coarse grains that must suppress welding heat affected zone (welded heat affected zone), therefore effectively in steel plate, disperse fine precipitate, utilize pinning effect (pinning effect).Therefore, the importantly management of Ti, N.
3. reducing the solid solution N in the fusion section of bonding layer, is effective to the low-temperaturetempering embrittlement that suppresses to be caused by follow-up welding.Therefore, for solid solution N is fixed as BN, stringent regulations B importantly.
4. in order to ensure the toughness of the excellence of welding heat affected zone in low-temperaturetempering embrittlement temperature zone, suppress delayed fracture, the alloying element amount of importantly suitably managing C, Mn, Cr, Mo, P etc.
The present invention studies in an 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, have 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%, Mo:0.05～1.0%, Nb:0.005～0.025%, Ti:0.005～0.03%, Al:0.1% are following, N:
0.0015～0.0060%, B:0.0003～0.0020%, hardenability index (hardenability index) DI* by formula (1) expression is more than 45, remainder is formed by Fe and inevitable impurity, and microtexture is take martensite as matrix phase.
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. such 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 W:0.05～1.0% 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% and V:0.1% 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 excellent toughness and the wear-resistant steel plate of delayed fracture resistance characteristics at the multi-run welding weld part, 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 is for improving martensitic hardness, guarantee the excellent important element of wearability, in order to obtain this effect, must containing more than 0.20%.On the other hand, surpass 0.30% if contain, then not only weldability is deteriorated, and because of the low-temperaturetempering of the fusion section in the multi-run welding weld part, toughness 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 due to the low-temperaturetempering that suppresses the fusion section in the multi-run welding weld part.In order to obtain such effect, must contain more than 0.05%.On the other hand, surpass 1.0% if contain, then the toughness of multi-run 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 produces, and make the toughness of multi-run welding weld part deteriorated.Therefore, take 0.010% as the upper limit, preferably reduce as far as possible.Should illustrate, make refining cost (refining cost) rise unfavorable to economy owing to exceedingly reducing P, 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 due to the low-temperaturetempering that suppresses the fusion section in the multi-run welding weld part.This is that when reheating the temperature province that the low-temperaturetempering embrittlement occurs, 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 descends.Therefore, be limited to 0.40～1.5% scope.Be preferably 0.40～1.2%.
Mo：0.05～1.0%
Mo significantly increases hardening capacity, to the effective element of mother metal high rigidityization.And, have the deteriorated effect of toughness due to the low-temperaturetempering that suppresses the fusion section in the multi-run welding weld part.In order to obtain such effect, be made as more than 0.05%.But, owing to surpassing 1.0%, then base metal tenacity, ductility and anti-welding breaking are caused negative impact, so be made as below 1.0%.Therefore, be limited to 0.05～1.0% scope.Be preferably 0.1～0.8%.
Nb：0.005～0.025%
Nb separates out as carbonitride (carbonitride), make the microtexture miniaturization of mother metal and multi-run welding weld part, and be to have fixing solid solution N concurrently and improve the toughness of multi-run welding weld part 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, then separate out thick carbonitride, become 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 the effect that TiN has thickization of the crystal grain in the fusion section that suppresses the multi-run welding weld part by fixing solid solution N, and has the effect of the generation that suppresses and delayed fracture 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, and is in the steel liquid deoxidation operation of steel plate, particularly commonly used.In addition, by the solid solution N in the fixing steel, form AlN, thereby have the effect of the coarse grains in the fusion section that suppresses the multi-run welding weld part, and have the effect of the generation that suppresses and delayed fracture deteriorated because of the toughness in the low tempering temperatures zone of solid solution N due to reducing.On the other hand, surpass 0.1% if contain, be blended into welding metal (weld metal) when then welding, make the toughness of welding metal deteriorated, therefore be limited to below 0.1%.Be preferably 0.01～0.07%.
N：0.0015～0.0060%
N is combined with Ti and is separated out as TiN, thereby suppresses thickization of the austenite grain of heat affected zone (HAZ), helps high malleableize.In order to ensure the requirement of the TiN with such effect, must contain the N more than 0.0015%.On the other hand, surpass 0.0060% if contain, then be heated to when welding in the zone of temperature of TiN dissolving, solid solution N measures increase, and the toughness in the low tempering temperatures zone is deteriorated to become remarkable.Therefore, N is limited to 0.0015～0.0060%.Be preferably 0.0020～0.0055%.
B：0.0003～0.0020%
B is that the interpolation with trace just can significantly increase hardening capacity, to the effective element of mother metal high rigidityization.And, have in when welding and be heated in the zone of temperature of TiN dissolving, solid solution N is fixed as BN, suppress because of the deteriorated effect of toughness in the low tempering temperatures zone due to the follow-up welding.In order to obtain such effect, be preferably more than 0.0003%, if surpass 0.0020%, then base metal tenacity, ductility and anti-welding breaking (weld crackresistance) are caused negative impact, therefore be made as below 0.0020%.Be preferably 0.0005～0.0018%.Remainder is Fe and inevitable impurity.
In the present invention, in order further to improve characteristic, on the basis of above-mentioned basal component system, can also contain one kind or two or more among W, Cu, Ni, V, REM, Ca, the Mg.
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%.
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%, if but surpass 1.5%, then effect is saturated, produces red brittleness (hot brittleness) 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%, if 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, add according to desirable characteristic selectivity.When adding REM, be preferably more than 0.002%, even if but also saturated above 0.008% effect, therefore take 0.008% as the upper limit.
When adding Ca, be preferably more than 0.0005%, even if but also saturated above 0.005% effect, therefore take 0.005% as the upper limit.
When adding Mg, be preferably more than 0.001%, even if but also saturated above 0.005% effect, 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 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 welding procedure 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 of the microtexture of steel plate is defined as martensite.Because the tissues such as the bainite (bainite) beyond the martensite, ferrite (ferrite) reduce wearability, so preferably do not mix as far as possible, if the total face integration rate (area ratio) of these tissues 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, preferred surface hardness is counted more than the 400HBW10/3000 with Brinell hardness (Brinell hardness).
In addition, in the steel of the present invention's exploitation, 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, in the steel of the present invention's exploitation, 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 that surrounds of the high-angle boundary more than 15 ° is lower than 70 μ m by the inclination angle.
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 300 ℃ tempering following condition under 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 the enforcement of part steel plate, 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 JISZ2202(1998) regulation, the direction vertical with rolling direction from thickness of slab 1/4 position of each steel plate, gather V notched specimen (Vnotch test specimen), based on JIS Z2242(1998) regulation each steel plate is implemented the Charpy impact test (Charpy impact test) of 3 of each temperature, obtain the absorption energy (absorbed energy) 0 ℃ of test temperature and-40 ℃, 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, implement rubber wheel test (rubber wheelabrasion test) and.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 test, after room temperature is placed 48 hours, gather 5 test board weld part cross-section samples (to 200mm welding bead progress row 5 five equilibriums), observing by projector and opticmicroscope (optical microscope) has flawless generation at welding heat affected zone.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 1-1 ］
The low-temperaturetempering that thermal cycling test (synthetic heat-affected zone test) is the fusion section when simulating the 2 layers of carbon dioxide arc welding that carries out welding heat input 17kJ/cm is reproduced in welding.Be implemented as follows thermal cycling: make the fusion section of 1 layer of welding (bonding layer) keep for 1 second at 1400 ℃, be 30 ℃/s the cooling time that makes 800～200 ℃, then as the low-temperaturetempering of 2 layers of welding (follow-up welding), 300 ℃ of 1 seconds of maintenance, make 300～100 ℃ to carry out 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 make test temperature be 0 ℃ each steel plate carried out with 3 test films.
To absorb energy (vE 0) the mean value of 3 test films be to be evaluated as HAZ tenacity excellent (in the scope of the invention) more than the 30J.
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 to be evaluated as HAZ tenacity excellent (in the scope of the invention) more than the 15J.
［ toughness of welded zone 1-2 ］
And, in order to confirm the toughness of actual joint, make multi-run welding welding joint (" レ " groove (レ shape groove)) with electrode arc welding (shielded metal arcwelding) (150 ℃ of temperature, welding material (welding material) between heat input (heat input) 17kJ/cm, 150 ℃ of preheatings, road: LB52UL(4.0mm Φ)).
From welding joint, the station acquisition Charpy impact test sheet of 1mm under the surface.Gap position (notch location) is the fusion area of the groove side vertical with surface of steel plate of " レ " groove.Use the test film that gathers like this, 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 (actual weld joint) makes test temperature be 0 ℃ to carry out with 3 test films.Absorb energy (vE 0) the mean value of 3 test films be the tenacity excellent (in the scope of the invention) that is evaluated as the multi-run welding weld part more than the 30J.
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 to be evaluated as fusion section tenacity excellent (in the scope of the invention) more than the 15J.
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, weld part reproduces and all has excellent toughness in thermal cycling test and the actual welding toughness, and 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.6～19) that is grouped into outside the scope of the invention.
Embodiment 2
After being modulated to 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, 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 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 the absorption energy 0 ℃ of test temperature and-40 ℃, estimate 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.
To (be sometimes referred to as vE at the absorption energy of 0 ℃ of test temperature 0) the mean value of 3 test films be that 30J is above and (be sometimes referred to as vE-at the absorption energy of test temperature-40 ℃ 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 is implemented.
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 with 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 ℃, implements 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 the weld part cross-section sample (long 200mm carries out 5 five equilibriums to welding bead) of 5 test boards, at welding heat affected zone flawless generation is arranged by projector and observation by light microscope.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 2 layers of carbon dioxide arc welding (two layer CO that welding heat input 17kJ/cm is carried out in simulation that thermal cycling test is reproduced in welding 2The low-temperaturetempering of the fusion section of the welding heat affected zone in the time of gas shielded arc welding).Be implemented as follows thermal cycling: make the fusion section of 1 layer of welding (bonding layer) keep for 1 second at 1400 ℃, the speed of cooling that makes 800～200 ℃ is 30 ℃/s, then as the low-temperaturetempering of 2 layers of welding (follow-up welding), 300 ℃ of 1 seconds of maintenance, make 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 that to make test temperature be 0 ℃ and-40 ℃, and each steel plate is carried out with 3 test films.
To 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 to be evaluated as HAZ tenacity excellent (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 HAZ tenacity excellent (in the scope of the invention) more than the 13J.
［ toughness of welded zone 2-2 ］
And, in order further to confirm the toughness of actual joint (actual weld joint), make multi-run welding welding joint (" レ " groove) with electrode arc welding (150 ℃ of temperature, welding material between heat input 17kJ/cm, 150 ℃ of preheatings, road: LB52UL(4.0mm Φ)).
From welding joint, the station acquisition Charpy impact test sheet of 1mm under the surface.Gap position is the fusion area of the groove side vertical with surface of steel plate of " レ " groove.Use the test film that gathers like this, 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 that to make test temperature be 0 ℃ and-40 ℃, carries out with 3 test films in 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 the tenacity excellent (in the scope of the invention) that is evaluated as the multi-run welding weld part 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, 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 to be evaluated as multi-run welding toughness of welded zone excellent (in the scope of the invention) more than the 13J.
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.20～22(wherein can to confirm the inventive example, No.22 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, in the toughness of weld part reproduction thermal cycling test and actual welding joint excellent toughness is arranged also, the multi-run welding 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.23, surface hardness, wearability, base metal tenacity are good, but T-shaped weld cracking expreiment, weld part reproduce thermal cycling test and the actual welding joint toughness will near the lower limit of target capabilities, be compared relatively poor with other example.For steel No.24, in becoming to be grouped into, Si outside the scope of the invention, although so surface hardness, wearability, base metal tenacity good, T-shaped weld cracking expreiment, weld part reproduce the thermal cycling test result and actual welding section toughness can't satisfy target capabilities.
Although steel No.25 becomes to be grouped within the scope of the present invention, but the parameter on the left side of formula (2): the value of C+Mn/4-Cr/3+10P surpasses 0.47, so weld part reproduction thermal cycling test result and actual welding joint toughness are compared relatively poor near the lower limit of target capabilities with other example.In addition, steel No.23 is into and is grouped in the scope of technical solution of the present invention 3 in table 4,5,6 record, but the value of DI* is outside the scope of technical solution of the present invention 6, therefore with it as a comparative example.Steel No.25 becomes to be grouped in the scope of technical solution of the present invention 1, but does not satisfy formula (2), outside the scope of technical solution of the present invention 7, therefore with it as a comparative example.
Figure BDA00002661792700181
Table 2
Annotate 1: underscore is outside the scope of the invention
Figure BDA00002661792700201
Figure BDA00002661792700211
Table 5
Figure BDA00002661792700221
Annotate 1: underscore is outside the scope of the invention
Figure BDA00002661792700231

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%, Mo:0.05～1.0%, Nb:0.005～0.025%, Ti:0.005～0.03%, Al:0.1% are following, N:0.0015～0.0060%, B:0.0003～0.0020%, 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 is characterized in that, described steel further contains W:0.05～1.0% in quality % in forming.
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, during described steel forms, in quality % further contain below the REM:0.02%, 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 formula (2), each symbol of element is the content in quality %.
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