CN105229190B - The high strength steel and its manufacturing method of excellent in fatigue characteristics - Google Patents
The high strength steel and its manufacturing method of excellent in fatigue characteristics Download PDFInfo
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- CN105229190B CN105229190B CN201480026771.6A CN201480026771A CN105229190B CN 105229190 B CN105229190 B CN 105229190B CN 201480026771 A CN201480026771 A CN 201480026771A CN 105229190 B CN105229190 B CN 105229190B
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/02—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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
The present invention relates to thick steel plates more than plate thickness 30mm, and provide the high strength steel and its manufacturing method of excellent in fatigue characteristics.A kind of high strength steel of excellent in fatigue characteristics, contain C:0.10~0.20%, Si:0.50% or less, Mn:1.0~2.0%, P:0.030% or less, S:0.0005~0.0040%, Sol.Al:0.002~0.07%, Ca:0.0005~0.0050% at being grouped as in terms of quality %, rest part is made of Fe and inevitable impurity, and metal structure is the ferrite of main phase and the bainite and pseudopearlite of the 2nd phase.
Description
Technical field
The present invention relates to the thick steel plate of plate thickness 30mm~50mm, be related to be suitable for ship, marine structure, bridge, building,
Repellence that tank etc. is strongly required the welded structure of safety of structure, that fatigue cracking generation and fatigue cracking develop is excellent
High strength steel and its manufacturing method.
Background technique
Steel used in the works such as ship, marine structure, bridge, tank, except the engineering properties such as intensity, toughness,
Other than welding property excellent, for the repetition load in usually working, the repeatedly vibration as caused by wind, earthquake etc., it is necessary to have knot
The safety of structure of structure object.
For repeating load, repeating to shake, it is desirable that excellent in fatigue characteristics.Especially, in order to prevent as component breakage
Final destruction, it is believed that the generation and development for the fatigue cracking for effectively steel being inhibited to have.
In the case where common welded structure, soldered edge easily becomes stress concentration portion, the drawing caused by welding
It stretches residual stress also to play a role, therefore becomes the generating source of fatigue cracking mostly.Strategy is prevented as it, it is known that soldered
Edge carries out welding (welding without welding rod) without welding rod, or imports compressed residual by peening
Stress.
However, welded structure has a large amount of soldered edge, in addition, also burden is big in cost.Therefore, these sides
Method is not suitable for implementing on an industrial scale, and the raising of the fatigue-resistance characteristics of welded structure passes through used steel itself mostly
The raisings of fatigue properties is realized.
Non-patent literature 1 is discussed to be repeated the special thermal treatment of laboratory scale and is manufactured with the steel for limiting ingredient
2 kinds of steel propagation of fatigue crack behavior.In the literature, investigate in detail and describe following item: to make hard phase (dimension
Family name's hardness: 565, phase divides rate: 36.4%, the average-size of phase: 149 μm) (Vickers hardness: uniformly divide in 148) in soft phase
Dissipate made of steel A and with hard phase (Vickers hardness: 546, phase divides rate: 39.2%) by soft phase (Vickers hardness: 149)
The propagation of fatigue crack for surrounding steel B made of mesh-shape is studied, as a result, the propagation of fatigue crack speed of steel B
Degree is greatly reduced.
A kind of steel plate for developing inhibitory effect with fatigue cracking is described in patent document 1, which is characterized in that hard portion
Matrix and be scattered in the soft part of the matrix and constitute metal structure, the difference of hardness of 2 part with Vickers hardness be calculated as 150 with
On.
A kind of thick steel plate that fatigue strength is excellent is described in patent document 2, which is characterized in that metal structure is by including iron
The organizational composition of ferritic and hard second phase, and the area of the above-mentioned hard second phase in the section structure parallel with surface of steel plate
Point rate is 20~80%, Vickers hardness is 250~800, average equivalent circular diameter is 10~200 μm, and between hard second phase
Largest interval is 500 μm or less.
A kind of expansionary excellent steel plate of fatigue cracking is described in patent document 3, which is characterized in that metal structure with
The area ratio is calculated as 60~85% bainite structure, adds up to 0~5% martensitic structure and pearlitic structrure, rest part
For ferritic structure.
Existing technical literature
Patent document
Patent document 1: No. 2962134 bulletins of Japanese Patent No.
Patent document 2: No. 3860763 bulletins of Japanese Patent No.
Patent document 3: No. 4466196 bulletins of Japanese Patent No.
Non-patent literature
Non-patent literature 1:H.SUZUKI AND A.J.MCEVILY:Metallurgical Transactions A,
Volume 10A, P475~481,1979
Summary of the invention
However, the steel recorded in non-patent literature 1 needs the heat treatment in 5 stages, in order to carry out work with industrial products scale
Journey produce and be unpractical from the viewpoint of cost, productivity.In addition, with propagation of fatigue crack characteristic mutually ductility instead
This steel can not be applied to works by decline.
About patent document 1,2, also using heat treatment before and after hot rolling, therefore in terms of the efficiency in engineering production
Not preferably.For example, in patent document 2, in order to improve the characteristic of thick-wall materials, implementing -2 phase region of diffusion heat treatments-hot rolling heat
Processing.
In patent document 3, using the smaller 15mm plate thickness material of plate thickness as object, the thickness of plate thickness 30mm or more is not corresponded to
Wall material.In order to ensure the intensity of thick-wall materials, need to add the alloying element of C etc..However, C amount is up in patent document 3
0.1%, it is possible to which intensity is insufficient in the case where wall thickening.
In addition, any of the above-described invention seek improve fatigue cracking generation and fatigue cracking it is developing any one, do not have
Have both the research of the steel plate of two kinds of characteristics.The inhibition that fatigue cracking generates increases female steel plate by increasing fatigue strength
Yield stress and improve.However, high strength steel, more becomes larger in the stress concentration of fatigue cracking apex and encourages tired tortoise
Split development.
Therefore, the present invention relates to the thick steel plate of plate thickness 30mm~50mm, and it is an object of the present invention to provide fatigue cracking generates and fatigue
The repellence developed that is cracked excellent steel and its manufacturing method.
Further investigation has been repeated to reach the above subject by the present inventor etc., even for plate thickness
The thick steel plate of 30mm~50mm also has the high-strength steel plate of excellent fatigue properties, obtains following opinion.
1. being greater than the thick steel plate of 30mm for plate thickness, in order to improve simultaneously, fatigue cracking is generated and fatigue cracking develops
Both characteristics of property, it is important that the mixing being made of the bainite and pseudopearlite of the ferrite of main phase and the 2nd phase is made
Tissue.This tissue can be realized by and condition and range appropriate is manufactured.In the present invention, by containing 0.10% with
On C amount, can steadily reach by the 2nd phase Line Integral rate increase caused by high intensity.
2. in turn, being controlled in order to ensure fatigue properties using the sulfide that Ca addition carries out for high-strength thick wall material
Effectively play a role.Ca fixes S and forming CaS, generates the complex inclusion with MnS.When MnS individualism, rolling
It is stretched when processed, becomes the starting point of destruction.However, by the way that CaS to be made to the complex inclusion with MnS, to imperceptibly disperse
In parent phase, the repellence of fatigue cracking generation and fatigue cracking development is improved.
The present invention is further to be studied above-mentioned opinion and made, and purport is as follows.
[1] a kind of high strength steel of excellent in fatigue characteristics, at be grouped as in terms of quality % containing C:0.10~0.20%,
Si:0.50% or less, Mn:1.0~2.0%, P:0.030% or less, S:0.0005~0.0040%, Sol.Al:0.002~
0.07%, Ca:0.0005~0.0050%, rest part are made of Fe and inevitable impurity, and metal structure is main phase
The bainite and pseudopearlite of ferrite and the 2nd phase.
[2] high strength steel of the excellent in fatigue characteristics as described in [1], which is characterized in that at being grouped as in terms of quality %
Further containing selected from one of Ti:0.003~0.03%, Nb:0.005~0.05% or two kinds.
[3] high strength steel of the excellent in fatigue characteristics as described in [1] or [2], which is characterized in that at being grouped as with matter
Measure % meter further containing selected from Cr:0.1~0.5%, Mo:0.02~0.3%, V:0.01~0.08%, Cu:0.1~
0.6%, one or more of Ni:0.1~0.5%.
[4] high strength steel of the excellent in fatigue characteristics as described in any one of [1]~[4], which is characterized in that at grouping
At further containing O:0.0040% hereinafter, and meeting following formula (1).
0 < (Ca- (0.18+130 × Ca) × O)/1.25/S≤0.8 (1)
Wherein, Ca, O, S in formula (1) indicate the content (quality %) of each ingredient.
[5] a kind of manufacturing method of the high strength steel of excellent in fatigue characteristics, which is characterized in that will have in [1]~[4]
It is described in any item be heated to 950~1250 DEG C at the steel raw material being grouped as after, in Ar3Or more carry out accumulation reduction ratio
50% or more rolling, with 5 DEG C/sec or more of cooling velocity from Ar3The temperature region acceleration of -60 DEG C or more of point is cooled to 350
DEG C~600 DEG C of temperature region.
[6] manufacturing method of the high strength steel of the excellent in fatigue characteristics as described in [5], which is characterized in that above-mentioned cooling
Speed is that there is the cooling curve in the CCT figure at the steel raw material being grouped as described in any one of above-mentioned [1]~[3] to be in
Below cooling velocity when ferrite transformation protruding portion.
[7] manufacturing method of the high strength steel of the excellent in fatigue characteristics as described in [5] or [6], which is characterized in that above-mentioned
After accelerating cooling, further with Ac1Point temperature below carries out tempering.
According to the present invention, fatigue cracking can be obtained to generate and fatigue cracking expansionary excellent steel and its manufacturer
Method.For example, can also delay propagation thereafter even if generating fatigue cracking year in year out from stress concentration portion, weld part etc. and improve
The safety of steel structure, it is industrially exceedingly useful.
Detailed description of the invention
Fig. 1 is the schematic diagram for indicating the CCT figure (continuous cooling transformation diagram) of steel raw material.
Specific embodiment
To it is of the invention at be grouped as, the regulation of manufacturing condition and metal structure is described in detail.
1. about at being grouped as
Hereinafter, being illustrated to of the invention at being grouped as.In addition, being all set to quality % at the % in being grouped as.
C:0.10~0.20%
For C, in order to obtain as intensity needed for structural steel, 0.10% or more content is needed.However, if containing
Amount is greater than 0.20%, then can damage weldability, therefore C amount is set as 0.10~0.20% range.Preferably 0.10~0.18%
Range.More preferably 0.11~0.17% range.
Si:0.50% or less
Si is the element beneficial as deoxidant element, by playing its effect containing 0.01% or more.However, if containing
Amount is greater than 0.50%, then the toughness of base material and welding heat affected zone is remarkably decreased, and weldability is remarkably decreased.Therefore, Si amount
It is set as 0.50% or less.Preferably 0.05~0.40% range.
Mn:1.0~2.0%
Mn is added from the viewpoint of ensuring strength of parent.However, its effect is not filled when amount is less than 1.0%
Point.In addition, excessively improving harden ability if amount is greater than 2.0%, being remarkably decreased the toughness of heat affected zone.Therefore, Mn
Amount is set as 1.0~2.0% range.Preferably 1.0~1.8% range.More preferably 1.0~1.6% range.
P:0.030% or less
If P amount is greater than 0.030%, it is remarkably decreased the toughness of base material and heat affected zone.Therefore, P amount is set as
0.030% or less.Preferably 0.02% or less.
S:0.0005~0.0040%
0.0005% or more is needed in order to generate required CaS or MnS for S, if amount is greater than 0.0040%,
Make the degraded toughness of base material.Therefore, S amount is set as 0.0005~0.0040% range.Preferably 0.001~0.0035% model
It encloses.More preferably 0.001~0.0030% range.
Sol.Al:0.002~0.07%
Sol.Al needs 0.002% or more in terms of the deoxidation of steel, preferably comprises 0.01% or more.However, if amount
Greater than 0.07%, then decline the toughness of base material.Therefore, Sol.Al amount is set as 0.002~0.07% range.Preferably
0.005~0.07% range.More preferably 0.01~0.06% range.
Ca:0.0005~0.0050%
Chemistry fixes S to Ca and forming CaS, generates the complex inclusion with MnS.When MnS individualism, in rolling
It is stretched, becomes the starting point of destruction.However, by the way that the complex inclusion with MnS is made, thus be imperceptibly scattered in parent phase,
The repellence of fatigue cracking generation and fatigue cracking development improves.In order to play this effect, need at least to contain 0.0005%
More than.However, effect can be also saturated even if amount is greater than 0.0050%.Therefore, Ca amount is set as 0.0005~0.0050%
Range.Preferably 0.001~0.0040% range.More preferably 0.001~0.0030% range.
It is basic chemical component of the invention above, rest part is made of Fe and inevitable impurity.In turn, to mention
For the purpose of high-intensitive, toughness, it can also contain and be selected from one or more of Ti, Nb alternatively element.
Ti:0.003~0.03%
In order to further increase toughness, Ti can be contained.TiN is generated when Ti heating before the rolling, makes austenite partial size
Miniaturization, improves toughness.Its effect is insufficient when its content is less than 0.003%, even if amount is greater than 0.03%, effect
It can be saturated.When therefore, containing Ti, Ti amount is preferably set to 0.003~0.03% range.
Nb:0.005~0.05%
In order to improve intensity, Nb can be contained.Its effect is insufficient when its content is less than 0.005%, if more than 0.05%,
Can then toughness be made to decline.When therefore, containing Nb, amount is preferably set to 0.005~0.05% range.More preferably 0.003~
0.030% range.
In turn, for the purpose of improving intensity, high strength steel of the invention can also contain and be selected from addition to above-mentioned composition
One or more of Cr, Mo, V, Cu, Ni alternatively element.
Cr:0.1~0.5%
Its effect is insufficient when Cr is less than 0.1%, if amount is greater than 0.5%, weldability decline.Therefore, containing Cr
When, Cr amount is preferably set to 0.1~0.5% range.More preferably 0.1~0.4% range.
Mo:0.02~0.3%
Its effect is insufficient when Mo is less than 0.02%, if amount is greater than 0.3%, weldability is remarkably decreased.Therefore, contain
When having Mo, Mo amount is preferably set to 0.02~0.3% range.More preferably 0.02~0.20% range.
V:0.01~0.08%
Its effect is insufficient when V is less than 0.01%, if amount is greater than 0.08%, toughness is remarkably decreased.Therefore, contain
When V, V amount is preferably set to 0.01~0.08% range.More preferably 0.01~0.07% range.
Cu:0.1~0.6%
Its effect is insufficient when Cu is less than 0.1%, if amount is greater than a possibility that 0.6%, Cu cracks and improves.Cause
This, when containing Cu, Cu amount is preferably set to 0.1~0.6% range.More preferably 0.1~0.3% range.
Ni:0.1~0.5%
Its effect is insufficient when the content of Ni is less than 0.1%, if amount is greater than 0.5%, the rising of steel product cost is aobvious
It writes.When therefore, containing Ni, Ni amount is preferably set to 0.1~0.5% range.More preferably 0.1~0.4% range.
O is preferably set as 0.0040% or less in addition to mentioned component forms by high strength steel of the invention.
O:0.0040% or less
If O amount is greater than 0.0040%, degraded toughness, therefore is set as 0.0040% or less.
High strength steel of the invention preferably further meets following formula (1).
0 < (Ca- (0.18+130 × Ca) × O)/1.25/S≤0.8 (1)
Wherein, Ca, O, S in formula indicate the content (quality %) of each ingredient.
Ca, O and S, which need to meet with above-mentioned formula (Ca- (0.18+130 × Ca) × O)/1.25/S, is greater than 0 and for 0.8 or less
The mode of relationship contain.In this case, become the form that the complex sulfide of MnS is precipitated on CaS.MnS is individually deposited
When, rolling when be stretched, become the starting point of destruction.However, by the way that CaS to be made to the complex inclusion with MnS, thus micro-
It is finely divided in parent phase, inhibit the generation of fatigue cracking.If the value of (Ca- (0.18+130 × Ca) × O)/1.25/S is greater than 0.8,
Then MnS is not generated, O and S all crystallizations in the form of Ca system oxysulfide.Therefore, size becomes thick, parent phase/field trash
The stress concentration at interface becomes larger and is difficult to ensure fatigue strength.When (Ca- (0.18+130 × Ca) × O)/1.25/S is 0 or less,
CaS is not crystallized, therefore S is precipitated in the form of MnS is individual, the MnS because steel plate manufacture when rolling due to be stretched, do not remain fine
Dispersion.Therefore, (Ca- (0.18+130 × Ca) × O)/1.25/S is set as greater than 0 and is 0.8 range below.
2. about metal structure
In order to realize the high intensity of tensile strength 510MPa or more, metal structure is substantially set as ferrite and bainite
With the line and staff control of pseudopearlite.The line and staff control of substantial ferrite and bainite and pseudopearlite is such as undertissue: they
Total Line Integral rate be 95% or more, as rest part, 5% martensite below, island are contained in terms of Line Integral rate
It is one kind or two or more in martensite, retained austenite etc..
In addition, main phase is the tissue for being greater than 50% in terms of Line Integral rate, the preferably ferritic Line Integral of the ferrite of main phase
Rate is 55% or more.In addition, the 2nd phase is tissue of the Line Integral rate less than 50%.
Preferably will for the thick-wall materials of plate thickness 30mm~50mm in order to realize the raising of high intensity and fatigue properties
Bainite and pseudopearlite as the 2nd phase is total with Line Integral rate score scattered 15% or more.By making in terms of Line Integral rate
15% or more, it can be expected that the raising of the intensity of base material, fatigue strength.In addition, pseudopearlite is relative to carbide and ferrite
Mutually disperse layered pearlite (lamelliform pearlite), thin layer shape disintegrate and carbide be bent, or be dispersed into it is block-like with
Tissue of the massive carbide as main body, sometimes also comprising a part of lamelliform carbide (relative to carbide total amount with area
Point rate is calculated as 40% or less).When thinking that the form of carbide is blocky, the case where relative to lamelliform, in parent phase/the 2nd phase boundary
The stress in face concentrates decline, and fatigue cracking, which generates, to be suppressed, and fatigue strength improves.
3. about manufacturing method
It is preferred that the steel with above-mentioned composition is carried out melting by well-established law with the meltings such as converter, electric furnace mechanism, continuously to cast
It makes method or ingot casting~cogging method etc. and the steel raw materials such as steel billet is made by well-established law.In addition, for method of smelting, casting, it is unlimited
Due to the above method.In addition, from the viewpoint of economy, preferably carrying out the steel making technology using converter process and utilizing continuous casting
Make the casting of the steel disc of technique.Thereafter, shape needed for being rolled into performance.Manufacturing condition of the invention described below.
The temperature condition of steel specified in the present invention refers to the mean temperature of steel disc or steel plate plate thickness direction.Plate thickness direction
Mean temperature is to be found out by plate thickness, surface temperature and cooling condition etc. by simulation calculating etc..For example, by using calculus of finite differences meter
The Temperature Distribution for calculating plate thickness direction, can find out the mean temperature in plate thickness direction.
(1) heating temperature: 950~1250 DEG C
When carrying out hot rolling, need to make steel disc fully austenitizing, therefore heating temperature is set as 950 DEG C or more.It is another
Aspect, if steel disc is heated to the temperature greater than 1250 DEG C, austenite grain starts coarsening, causes adverse effect to toughness,
Therefore heating temperature is set as 950~1250 DEG C of range.From the viewpoint of toughness, the range of preferred heating temperature is 1000
DEG C~1100 DEG C.
(2) in Ar3Or more accumulation reduction ratio: 50% or more
In rolling, improve toughness in order to which crystal grain is maintained fine, in Ar3Or more temperature region import processing
Deformation.For accumulating reduction ratio, by being set as 50% or more, the ferrite crystal grain after phase transformation sufficiently miniaturize and realizes toughness and mention
It is high.Therefore, by the accumulation reduction ratio in rolling in Ar3Or more be set as 50% or more.It should be noted that Ar3Point passes through following formula
(2) it finds out.
Ar3=910-310 [%C] -80 [%Mn] -20 [%Cu] -55 [%Ni] -15 [%Cr] -80 [%Mo] (2)
Here, each element symbol refers to the content (quality %) of each element, without containing the case where be set as 0.
When hot-rolled temperature is lower than ferrite transformation start temperature, pressure generates ferrite in the process and intensity declines, therefore
Hot rolling terminates temperature and is at least set as Ar3Or more.
(3) cooling start temperature: Ar3- 60 DEG C or more of point
If cooling start temperature is too low, cooling last stage ferrite production quantity is being accelerated to get higher, intensity decline.Cause
This, from Ar3- 60 DEG C or more of temperature is begun to cool.
(4) cooling velocity: 5 DEG C/sec or more
Continue to implement to accelerate cooling after hot rolling.By the way that cooling velocity is set as 5 DEG C/sec or more, no coarsening is organized, it can
Sappy structure is obtained, the excellent intensity, toughness and fatigue properties as target can be obtained.When cooling velocity is less than 5 DEG C/sec,
Organizational coarseness, and ferrite point rate becomes larger, and is unable to get strength of parent, fatigue strength, fatigue cracking as target
It is expansionary.In addition, the upper limit as cooling velocity, it is however preferred to have cold in the CCT figure of the steel raw material of mentioned component composition
But below cooling velocity when curve is in ferrite transformation protruding portion.Cooling velocity is greater than in ferrite transformation protruding portion
When cooling velocity, bainite point rate is got higher, and is unable to get expansionary fatigue cracking as target, ductility of base material and tough
Property.Tissue needed in order to obtain, plate thickness is preferably 30mm~50mm within the scope of the cooling velocity.
In addition, CCT figure (continuous cooling transformation diagram) is made up of following usual way: from what is formed with mentioned component
Steel acquire the cylindrical sample of multiple 8 × 12mm of φ, processed in hot-working reproduction test device with corresponding with rolling and
Refrigerating mode under various cooling velocities carries out processing and heat treatment, at the same the expansion of measurement test piece and investigate phase transition temperature.It asks
(cooling velocity in the region of ferrite transformation occurs for the ferrite transformation protruding portion by resulting CCT figure as shown in Figure 1 out
Most fast side) constant cooling velocity curve (CCT figure due to horizontal axis (time) be logarithm, become curve) cooling
Speed.In the present invention, cooling speed when ferrite transformation protruding portion is in 5 DEG C/sec or more and for the cooling curve in CCT figure
It spends cooling velocity below to be cooled down, to generate pseudopearlite, fatigue strength is improved.
(5) the cooling temperature that stops: 600~350 DEG C
Stop temperature by that will cool down and be set as 350 DEG C~600 DEG C, can be formed and be obtained by hot rolling and subsequent cooling
Required tissue.If the cooling temperature that stops is higher than 600 DEG C, bainite, pseudopearlite dispersion amount become inadequate, if being lower than
350 DEG C, then it is difficult to ensure ductility toughness.Stop temperature as cooling down, further preferably 400 DEG C~550 DEG C.
(6) tempering temperature: Ac1Or less
Need to carry out steel shape amendment or ductility, toughness raising when, can accelerate it is cooling after to be less than Ac1
Point is tempered.If tempering temperature is greater than Ac1Point then generates island-like martensite, degraded toughness.In addition, Ac1Point passes through following formula
(3) it finds out.
Ac1=723-11 [%Mn]+29 [%Si] -17 [%Ni]+17 [%Cr] (3)
Here, each element symbol refers to the content (quality %) of each element, without containing the case where be set as 0.
Embodiment 1
For, at the steel disc being grouped as, the confession of 30~50mm of plate thickness being made under the manufacturing condition shown in table 2 shown in table 1
Steel is tried, metal structure observation, engineering properties and the fatigue strength, fatigue cracking developing characteristics of resulting steel plate are investigated.In addition,
Cooling velocity when cooling curve in CCT figure (continuous cooling transformation diagram) is in ferrite transformation protruding portion is by following logical
Normal method is made and finds out: from the cylindrical sample for acquiring multiple 10 × 12mm of φ shown in table 1 at the steel being grouped as
Product are processed in hot-working reproduction test device with the refrigerating mode under processing corresponding with rolling and various cooling velocities
Heat treatment, at the same the expansion of measurement test piece and investigate phase transition temperature.
[table 1]
[table 2]
Structure observation is to utilize 3% nitric acid ethyl alcohol from sample made of the sample of arbitrary station acquisition using grinding
Implement 1/4 position of plate thickness in the etched rolling direction section of corrosive liquid (section L).In addition, being surveyed by optical microphotograph sem observation
Determine the area ratio of ferrite, bainite, pseudopearlite.These values are to be implemented to 1 sample with 5 visuals field, in the total of them
The form of the average value in the visual field is found out.
Tensile properties are used in distance 200mm between rolling direction and total thickness × punctuate of right angle orientation (direction C) acquisition
Test film (NKV1 test film), according to NK ship's classification K regulations implement tension test, find out tensile properties.
Toughness is by 2mmV v notch v Charpy-type test piece (NKV4 test film) from 1/4 position of plate thickness and rolling direction
It acquires in parallel, implements Charpy-type test according to NK ship's classification K regulations, 3 s' at -40 DEG C of test temperature is averaged
Value (vE-40 (J)) is evaluated.
Fatigue strength is using the pole tension test sheet of distance 24mm between φ 12mm × punctuate, with 100 Wan Ciying repeatedly
Value when power load is evaluated.For test film, according to JIS Z2273, plate thickness 50mm material from 1/4 station acquisition of plate thickness,
Plate thickness 30mm material is from 1/2 station acquisition of plate thickness.
Fatigue cracking developing characteristics are to be sent out with being cracked to the direction C according to ASTM E647 using the CT test film of plate thickness 25mm
Fatigue cracking development test when exhibition is investigated.For test film, plate thickness 50mm material is from 1/4 station acquisition of plate thickness, plate thickness
30mm material is from 1/2 station acquisition of plate thickness.Experimental condition is carried out in stress ratio 0.1, atmosphere at room temperature, is evaluated in Amplification
The interior 25MPam of coefficient range (Δ K)1/2When fatigue cracking development speed.
Test result is shown in table 3.
[table 3]
Test result is with yield stress YS:390N/mm2Above, tensile strength TS:510N/mm2Above, elongation:
19% or more, vE-40:100J or more, fatigue strength: 340Mpa or more, fatigue cracking development speed: 1.0 × 10-7(m/ circulation)
Below as qualified or not determinating reference.
Confirmed by table 3, No.1-1~8-1 as example of the present invention is that yield stress YS is 390N/mm2Above, it stretches
Intensity TS is 510N/mm2More than, there is excellent base material characteristic.In addition, the fatigue strength of steel of the present invention is 340MPa or more,
Fatigue cracking development speed is 1.0 × 10-7(m/ circulation) is hereinafter, fatigue properties are also excellent.On the other hand, as chemical component,
Manufacturing condition deviates No.9-1~12-1 of the comparative example of the scope of the present invention, it is above-mentioned in any above characteristic it is poor.
Embodiment 2
For, at the steel disc being grouped as, the confession of 30~50mm of plate thickness being made under the manufacturing condition shown in table 5 shown in table 4
Steel is tried, metal structure observation, engineering properties and the fatigue strength, fatigue cracking developing characteristics of resulting steel plate are investigated.In addition,
Cooling velocity when cooling curve in CCT figure (continuous cooling transformation diagram) is in ferrite transformation protruding portion is by following logical
Normal method is made and finds out: from the cylindrical sample for acquiring multiple 10 × 12mm of φ shown in table 4 at the steel being grouped as
Product are processed in hot-working reproduction test device with the refrigerating mode under processing corresponding with rolling and various cooling velocities
Heat treatment, at the same the expansion of measurement test piece and investigate phase transition temperature.
[table 4]
[table 5]
Structure observation is to utilize 3% nitric acid ethyl alcohol from sample made of the sample of arbitrary station acquisition using grinding
Implement 1/4 position of plate thickness in the etched rolling direction section of corrosive liquid (section L).In addition, being surveyed by optical microphotograph sem observation
Determine the area ratio of ferrite, bainite, pseudopearlite.These values are to be implemented to 1 sample with 5 visuals field, in the total of them
The form of the average value in the visual field is found out.
Tensile properties are used in distance 200mm between rolling direction and total thickness × punctuate of right angle orientation (direction C) acquisition
Test film (NKV1 test film), according to NK ship's classification K regulations implement tension test, find out tensile properties.
Toughness is by 2mmV v notch v Charpy-type test piece (NKV4 test film) from 1/4 position of plate thickness and rolling direction
It acquires in parallel, implements Charpy-type test according to NK ship's classification K regulations, 3 s' at -40 DEG C of test temperature is averaged
Value (vE-40 (J)) is evaluated.
Fatigue strength is using the pole tension test sheet of distance 24mm between φ 12mm × punctuate, with 100 Wan Ciying repeatedly
Value when power load is evaluated.For test film, according to JIS Z2273, plate thickness 50mm material from 1/4 station acquisition of plate thickness,
Plate thickness 30mm material is from 1/2 station acquisition of plate thickness.
Fatigue cracking developing characteristics are to be sent out with being cracked to the direction C according to ASTM E647 using the CT test film of plate thickness 25mm
Fatigue cracking development test when exhibition is investigated.For test film, plate thickness 50mm material is from 1/4 station acquisition of plate thickness, plate thickness
30mm material is from 1/2 station acquisition of plate thickness.Experimental condition is carried out in stress ratio 0.1, atmosphere at room temperature, is evaluated in Amplification
The interior 25MPam of coefficient range (Δ K)1/2When fatigue cracking development speed.
Test result is shown in table 6.
[table 6]
Test result is with yield stress YS:390N/mm2Above, tensile strength TS:510N/mm2Above, elongation:
19% or more, vE-40:100J or more, fatigue strength: 340Mpa or more, fatigue cracking development speed: 8.5 × 10-8(m/
Cycle) below as qualified or not determinating reference.
Confirmed by table 6, No.1-2~8-2 as example of the present invention is that yield stress YS is 390N/mm2Above, it stretches
Intensity TS is 510N/mm2More than, there is excellent base material characteristic.In addition, the fatigue strength of steel of the present invention is 340MPa or more,
Fatigue cracking development speed is 8.5 × 10-8(m/ circulation) is hereinafter, fatigue properties are also excellent.It may be said that by formula (1) be greater than 0 and
For 0.8 hereinafter, the expansionary more excellent high strength steel of fatigue cracking can be obtained.On the other hand, as chemical component, system
Make No.9-2~16-2 that condition deviates the comparative example of the scope of the invention, it is above-mentioned in any above characteristic it is poor.
Claims (8)
1. a kind of high strength steel of excellent in fatigue characteristics, plate thickness is 30mm~50mm, in terms of quality %, at being grouped as containing C:
0.10~0.20%, Si:0.50% or less, Mn:1.0~2.0%, P:0.030% or less, S:0.0005~0.0040%,
Sol.Al:0.002~0.07%, Ca:0.0005~0.0050%, rest part are made of Fe and inevitable impurity, gold
Belonging to tissue is the ferrite of main phase and the bainite and pseudopearlite of the 2nd phase, and the ferritic Line Integral rate of main phase is 55%
More than, the bainite of the 2nd phase and total Line Integral rate of pseudopearlite are 15% or more,
Fatigue cracking development speed is 1.0 × 10-7M/ circulation is following.
2. the high strength steel of excellent in fatigue characteristics as described in claim 1, which is characterized in that in terms of quality %, at grouping
At further containing selected from one of Ti:0.003~0.03%, Nb:0.005~0.05% or two kinds.
3. the high strength steel of excellent in fatigue characteristics as claimed in claim 1 or 2, which is characterized in that in terms of quality %, ingredient
Composition further containing selected from Cr:0.1~0.5%, Mo:0.02~0.3%, V:0.01~0.08%, Cu:0.1~0.6%,
One or more of Ni:0.1~0.5%.
4. the high strength steel of excellent in fatigue characteristics as claimed in claim 1 or 2, which is characterized in that in terms of quality %, ingredient
Composition further contain O:0.0040% hereinafter, and meet following formula (1),
0 < (Ca- (0.18+130 × Ca) × O)/1.25/S≤0.8 (1),
Wherein, Ca, O, S in formula (1) indicate the content of each ingredient, wherein the content of each ingredient is in terms of quality %.
5. the high strength steel of excellent in fatigue characteristics as claimed in claim 3, which is characterized in that in terms of quality %, at grouping
At further contain O:0.0040% hereinafter, and meet following formula (1),
0 < (Ca- (0.18+130 × Ca) × O)/1.25/S≤0.8 (1),
Wherein, Ca, O, S in formula (1) indicate the content of each ingredient, wherein the content of each ingredient is in terms of quality %.
6. a kind of manufacturing method of the high strength steel according to any one of claims 1 to 5 of excellent in fatigue characteristics, feature
Be, by with it is according to any one of claims 1 to 5 be heated to 950~1250 DEG C at the steel raw material being grouped as after,
Ar3Or more carry out accumulation reduction ratio be 50% or more rolling, hot rolling is terminated into temperature and is set as Ar3Or more, with 5 DEG C/sec with
On cooling velocity from Ar3The temperature region of -60 DEG C or more of point accelerates to be cooled to 350 DEG C~600 DEG C of temperature region.
7. the manufacturing method of the high strength steel of excellent in fatigue characteristics as claimed in claim 6, which is characterized in that the cooling
Speed is the cooling curve having in the CCT figure according to any one of claims 1 to 5 at the steel raw material being grouped as
Below cooling velocity when in ferrite transformation protruding portion.
8. the manufacturing method of the high strength steel of excellent in fatigue characteristics as claimed in claims 6 or 7, which is characterized in that described
After accelerating cooling, further with Ac1Point temperature below carries out tempering.
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| PCT/JP2014/003380 WO2014208082A1 (en) | 2013-06-25 | 2014-06-24 | High-strength steel material having excellent fatigue properties, and method for producing same |
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