JP2006283187A - Production method of high-strength/high-toughness steel - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a production method of a high-strength/high-toughness steel which is suitable for welded structures of shipbuilding, ocean structures, construction machinery, buildings, bridges, tanks, steel pipes and hydraulic iron pipes, etc., of 590 MPa tensile strength and has excellent strength and toughness balance. <P>SOLUTION: In the production method, a steel stock material having the composition containing, by mass%, 0.01 to 0.20% C, 0.01 to 0.80% Si, 0.5 to 2.50% Mn, ≤0.020% P, ≤0.0070% S, 0.004 to 0.100% Sol.Al, and if necessary containing one or two or more kinds of Cu, Ni, Cr, Mo, Nb, V, B, Ca, Mg, and REM, and consisting of the balance Fe and inevitable impurities is subjected to hot rolling having a rolling end temperature at a temperature region of Ar<SB>3</SB>transformation point or above, then to heat treatment at a heating rate of ≥1°C/s up to a reheating temperature and within 90 seconds of the stagnation time in a temperature region of Ac<SB>1</SB>to Ac<SB>1</SB>+150°C after hardening to ≤300°C from the temperature region of Ar<SB>3</SB>transformation point or above. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

The present invention relates to a method for producing high-strength and high-toughness steel having an excellent strength-toughness balance, and particularly to welded steel structures such as shipbuilding, marine structures, construction machinery, architecture, bridges, tanks, steel pipes, and hydraulic iron pipes. The present invention relates to a suitable method for producing a thick steel plate to be used.

  Generally, as the strength of a steel plate increases, the toughness tends to decrease. In particular, it is difficult to provide good low-temperature toughness in a high-strength steel sheet having a tensile strength of 590 MPa or more. Therefore, many studies have been made to ensure high strength and low temperature toughness for high strength thick steel plates having a tensile strength of 590 MPa or more.

  For example, as disclosed in Patent Document 1, by obtaining a mixed structure of fine ferrite, bainite or martensite from a fine γ phase by direct quenching and short-time tempering in a high strength steel of 60 to 70 kilo class. Achieve toughness.

Moreover, in the high strength steel of 90 kg or more disclosed in Patent Document 2, the Nb and Mn amounts are limited and good toughness is ensured by the quenching and tempering treatment. All of these devise quenching from rolling and tempering at a temperature of Ac ₁ or lower in order to use the precipitation strengthening ability of Nb and toughness deterioration due to Nb precipitation in a well-balanced manner.

On the other hand, Patent Document 3 proposes that the heating rate in tempering after quenching is increased, and tempering is performed at a temperature of Ac ₁ or less while securing dislocations obtained by rolling or quenching, thereby achieving toughening. ing.
Japanese Examined Patent Publication No. 61-60891 JP-A-2-209422 Japanese Examined Patent Publication No. 7-74380

As described above, in the prior art, it has been studied to control the conditions in the quenching process and the tempering process at a temperature of Ac ₁ or lower to ensure a predetermined strength to toughness, but suppress the strengthening ability such as Nb. However, in order to ensure toughness, certain limits occur in the strength and toughness obtained, and when the tensile strength exceeds 1200 MPa, it is difficult to adjust the strength / toughness balance.

  The present invention solves the problems of the prior art, and proposes a method for producing a high strength and high toughness steel having a high strength of a tensile strength of 590 MPa or more and far exceeding the conventional level in the strength-toughness balance. Objective.

  In order to solve the above problems, the present inventors have intensively studied paying attention to the characteristics in the tempering process. As a result, in the tempering process in high-strength steel, the martensite structure or the mixed structure of martensite and bainite is tempered. There is a limit to restricting the amount and size of precipitates without losing strength, when recovery and recovery, and mainly carbide precipitation occurs, it is effective to make the structure itself a fine structure I found.

That is, as the tempering temperature, Ac ₁ which was thought to be impossible to be toughened due to island-like martensite formed after cooling due to C decreasing in strength or reversely transformed austenite. Considering reheating to higher temperatures, and as a result, by controlling the specific temperature, heating rate, and residence time in the two-phase region, the structure at the time of quenching is finely divided and the strength is kept high. We found that toughening is possible.

The present invention takes advantage of the fact that a fine martensite structure or a lower bainite structure different from the crystal orientation of the prior γ grains is obtained at the time of cooling without giving time for C to concentrate in the reverse transformation structure. Unprecedented high strength and high toughness were achieved by making the fracture surface units finer.
That is, the gist of the present invention is as follows.
1. % By mass, C: 0.01 to 0.20%,
Si: 0.01-0.80%,
Mn: 0.5-2.50%,
P: 0.020% or less,
S: 0.0070% or less,
sol. Al: 0.004 to 0.100%
And a steel material having the balance of Fe and inevitable impurities is subjected to hot rolling with the rolling end temperature set to a temperature range equal to or higher than the Ar ₃ transformation point, and then to a temperature range equal to or higher than the Ar ₃ transformation point. from after quenching to 300 ° C. or _less, Ac ₁ when reheating to to Ac temperature range of 1 + 0.99 ° C., heating rate of up to reheating temperature at 1 ° C. / s or more and _Ac 1 _~Ac 1 + 150 ℃ temperature range of A method for producing high-strength and high-toughness steel, characterized by performing a heat treatment in which the residence time is 90 seconds or less.
2. In addition to the steel composition, in mass%, Ti: 0.005 to 0.20%
Cu: 0.01 to 2.0%
Ni: 0.01-4.0%
Cr: 0.01 to 2.0%
Mo: 0.01 to 2.0%
Nb: 0.003 to 0.1%
V: 0.003-0.5%
B: 0.0005 to 0.0040%
Ca: 0.0001 to 0.0060%
Mg: 0.0001 to 0.0060%
REM: 0.0001 to 0.0200%
The method for producing high-strength and high-toughness steel according to 1, characterized by containing one or more of the above.
3. The method for producing high-strength and high-toughness steel according to 1 or 2, wherein the heat treatment performed after quenching is accelerated and cooled at least in a temperature range from the Ac ₁ transformation point to 600 ° C. or lower after heating and holding.
4). 4. The method for producing high strength and high toughness steel according to 3, wherein tempering is further performed after accelerated cooling.
5. The method for producing high-strength and high-toughness steel according to any one of 1 to 4, wherein the process from the cooling stop during quenching to the start of reheating is continuously performed within 180 seconds.

According to the present invention, tempering is performed at a temperature exceeding Ac _1, and strength reduction is minimized by controlling the heating rate, temperature, and residence time, and the fine division of the fracture surface unit by the reverse transformation structure is enabled. Thus, a high strength and high toughness steel excellent in strength-toughness balance having a high strength with a tensile strength of 590 MPa or more and a high toughness with a fracture surface transition temperature vTrs of ˜40 ° C. or less is obtained, which is extremely useful industrially.

Hereinafter, the present invention will be described in detail. % In the component composition is mass%.
[Ingredient composition]
C: 0.01 to 0.20%
In order to secure the strength of the steel sheet, at least 0.01% is necessary for C, and if added over 0.20%, the weldability is remarkably lowered, so 0.01% or more and 0.20% or less (hereinafter, 0.01 to 0.20%).

Si: 0.01-0.80%
Si is an element necessary for deoxidation, but if less than 0.01%, the effect is small, and if added over 0.80%, weldability and base metal toughness are remarkably lowered, so 0.01 to 0.00%. 80%.

Mn: 0.5-2.50%
Mn is necessary for securing the strength of the steel sheet in the same manner as C. If excessively added, the weldability is impaired, so 0.5 to 2.50%.

P: 0.020% or less, S: 0.0070% or less P and S are elements inevitably contained in the steel as impurities, in order to deteriorate the toughness of the steel base material and the weld heat affected zone. It is preferable to reduce as much as possible in consideration of economy, and P: 0.020% or less, S: 0.0070% or less.

Al: 0.004 to 0.10% or less Al is a deoxidizing element, and if it is less than 0.004%, its effect is not sufficient, and if added excessively, toughness is deteriorated, so 0.004 to 0.10 % Or less.

  Although the basic component composition of the present invention is as described above, when further improving desired characteristics, one or more of Ti, Cu, Ni, Cr, Mo, Nb, V, B, Ca, Mg, and REM are used. Add as selective element.

Ti: 0.005 to 0.20%
Ti has a predetermined range from the viewpoint of ensuring the toughness of the base metal and ensuring the toughness in the heat affected zone, but if added over 0.20%, the toughness is significantly reduced. 0.005 to 0.20%.

Cu: 0.01 to 2.0%
Cu is an element for increasing the strength and exerts its effect at 0.01% or more, and if added over 2.0%, the steel sheet surface properties deteriorate due to hot brittleness. 0.01 to 2.0%.

Ni: 0.01-4.0%
Ni can improve the toughness while increasing the strength of the base metal, and exhibits an effect at 0.01% or more, and the effect is saturated and economically disadvantageous at 4.0% or more. Is 0.01 to 4.0%.

Cr: 0.01-2.0%, Mo: 0.01-2.0%
Both Cr and Mo are effective in increasing the strength, and when 0.01% or more, the effect is exerted. When added over 2.0%, the toughness deteriorates remarkably. Respectively 0.01 to 2.0%.

Nb: 0.003-0.1%, V: 0.003-0.5%
Nb and V are elements that improve the strength and toughness of the base material, and exhibit an effect when added in an amount of 0.003% or more. Further, if it exceeds 0.1% and 0.5%, respectively, the toughness may be lowered. Therefore, when added, Nb: 0.003 to 0.1%, V: 0.003 to 0.5 %.

B: 0.0005 to 0.0040%
B can increase the strength by improving the hardenability. This effect becomes prominent at 0.0005% or more, and the effect is saturated even if added over 0.0040%. Therefore, when added, the content is made 0.0005 to 0.0040%.

Ca: 0.0001 to 0.0060%, Mg: 0.0001 to 0.0060%, REM: 0.0001 to 0.0200%
Ca, Mg. REM has the function of fixing S in steel and improving the toughness of the steel sheet, and is effective when added in an amount of 0.0001% or more. However, if added over 0.0060%, 0.0060%, and 0.0200%, respectively, the amount of inclusions in the steel increases and deteriorates the toughness, so when added, Ca: 0.0001-0. 0060%, Mg: 0.0001 to 0.0060%, REM: 0.0001 to 0.0200%.

  The balance other than the components described above consists of Fe and inevitable impurities.

[Production conditions]
The molten steel having the above composition is melted by a conventional method using a melting means such as a converter or an electric furnace, and is made into a steel material such as a slab by a conventional method using a continuous casting method or an ingot-bundling method. preferable. In addition,
The melting method and the casting method are not limited to the methods described above. Then, after rolling into a desired shape, quenching and tempering are performed.

1. Rolling Rolling is performed to make a steel material such as a slab into a desired shape, and the end temperature is set to a temperature range equal to or higher than the Ar ₃ transformation point in order to obtain a fine quenched structure.

2. Quenching In order to make the structure after quenching a martensite-based structure, it is quenched from a temperature of ₃ or more Ar to a temperature of 300 ° C. or less.
When quenching from a temperature of ₃ points or less of Ar, ferrite partly precipitates, so that the strength decreases greatly during reheating heat treatment, and a predetermined strength cannot be obtained.

3. Tempering In tempering, the structure after quenching is changed to a fine martensite structure or lower bainite structure different from the crystal orientation of the former austenite (γ) grains by reverse transformation, and the fracture surface units are finely divided to improve toughness. _Therefore, heating to a temperature range of Ac ₁ ~Ac ₁ + 150 ℃.

  The former austenite (γ) grains here are divided by a fine grain size of austenite (γ) during rolling and fine precipitation of retransformed austenite (γ) during tempering. Steel with a martensite-based structure has high toughness by making the former austenite (γ) grain size finer, but breaks when the former austenite (γ) grain size exceeds 30 μm. The fracture surface unit becomes larger, leading to a decrease in toughness.

  When the heating rate is less than 1 ° C./s, a significant decrease in strength is caused by the disappearance and recovery of dislocations until the predetermined heating temperature is reached, and C is concentrated in the reverse transformation structure to deteriorate toughness. 1 ° C./s or more. If the residence time exceeds 90 s in this temperature range, the strength is reduced, so the residence time is within 90 s. The heating temperature is an average heating rate from the start to the end of reheating.

Here, the steel temperature in the present invention indicates the average temperature of the surface and the central portion of the steel material, the entire steel material not heated to _Ac 1 ~Ac 1 + ₁₅₀ ℃, steel central part 400 ° C. or higher Ac ₁ Even when tempered to less than the above, the effect of the present invention can be obtained because the tempered martensite at the center of the quenching speed is high toughness and the toughness of the surface is important for the toughness of the steel material. Therefore, in the present invention, it is not always necessary to heat the entire steel material to Ac ₁ to Ac ₁ + 150 ° C.

Further, in the cooling process of the heat treatment exceeding Ac ₁ , even if accelerated cooling is performed at a cooling rate higher than air cooling at least in a temperature range from Ac ₁ to 600 ° C., equivalent performance can be obtained.

In order to suppress the toughness degradation due to the hard phase generated when an accelerated cooling may be further performed tempered at Ac ₁ temperature below if necessary.

The heat treatment (tempering) for heating to a temperature of Ac ₁ or higher performed after quenching is effective even after re-heating after cooling to room temperature after quenching, but preferably after cooling to 300 ° C. or less, within 180 s from cooling stop When reheating treatment is started continuously, it is easy and preferable to obtain high strength and high toughness from the viewpoint of securing dislocation density and preventing the coarsening of precipitates.

  If it exceeds 180 s, the strength decreases due to the dislocation opening, and the growth of carbides such as cementite occurs due to the diffusion of C, so that the starting point of fracture tends to be coarse and the toughness tends to decrease.

In quenching and tempering, Ar ₃ and Ac ₁ can be obtained by using the following equations. However, in each formula, each element shows the amount of addition: mass%.
Ar ₃ = 910-273C-74Mn-56Ni-16Cr-9Mo-5Cu
_{Ac 1 = 751-26.6C + 17.6Si-11.6Mn} -169Al-23Cu-23Ni + 24.1Cr + 22.5Mo + 233Nb-39.7V-5.7Ti-895B
The present invention is applicable to steel products having various shapes such as thick plates, section steels, and steel bars. “Thick plate” refers to a steel plate having a thickness of 6 mm or more.

  Molten steel having the composition shown in Table 1 was melted in a converter to obtain a slab (steel material) having a thickness of 250 mm by a continuous casting method, and a steel plate having a thickness of 6 to 60 mm was produced according to the hot rolling conditions shown in Table 2. In Table 1, any of the component compositions of the test steels with steel symbols AC, AD, AE, AF, and AG is outside the scope of the present invention.

  About the obtained thick steel plate, a micro tensile test piece of 6φ was taken from a position in the plate thickness direction 1/2, and a tensile test was performed in accordance with the provisions of JIS Z 2241 (1998). The 0.2% yield strength YS was determined.

  In addition, a Charpy impact test specimen having a V-notch standard dimension was taken from a position in the plate thickness direction 1/2 in accordance with JIS Z 2202 (1998), and compliant with JIS Z 2242 (1998). The impact test was carried out to determine the fracture surface transition temperature vTrs. However, for a plate thickness of 11 mmt or less, vTrs was obtained using a half-size Charpy test piece.

  Further, a specimen for observing the structure was collected from the center of the plate thickness, and the average prior austenite (γ) particle size of the two-phase region heating part was measured by a line segment method with a scanning electron microscope and a transmission electron microscope.

  Table 3 shows the results of these tests. The average prior austenite (γ) particle size: 30 μm or less, tensile strength TS: 590 MPa or more, yield strength YS: 500 MPa or more, and toughness (vTrs): −40 ° C. or less were taken as examples of the present invention.

  Steel plate No. 1 in which either the composition of the component or the manufacturing condition is out of the scope of the present invention. Nos. 29 to 41 are steel plate Nos. 1-28, no. Compared to 42 to 45, the average prior austenite (γ) particle size is large, and at least one characteristic of tensile strength TS, yield strength YS and toughness is inferior.

No. 51 and no. 52, No. 52, respectively. 2 and no. Under the same conditions as 14, an embodiment in the case where accelerated cooling the Ac ₁ to 600 ° C. below the temperature range after tempering, good performance is obtained.

No. 53 is No. _No. 52 in the case of further tempering after tempering (accelerated cooling) of Ac ₁ or higher. An improvement in toughness was observed with respect to 52. No. 51-No. 53 is within the scope of the present invention.

Claims (5)

% By mass, C: 0.01 to 0.20%,
Si: 0.01-0.80%,
Mn: 0.5-2.50%,
P: 0.020% or less,
S: 0.0070% or less,
sol. Al: 0.004 to 0.100%
And a steel material having the balance of Fe and inevitable impurities is subjected to hot rolling with the rolling end temperature set to a temperature range equal to or higher than the Ar ₃ transformation point, and then to a temperature range equal to or higher than the Ar ₃ transformation point. from after quenching to 300 ° C. or _less, Ac ₁ when reheating to to Ac temperature range of 1 + 0.99 ° C., heating rate of up to reheating temperature at 1 ° C. / s or more and _Ac 1 _~Ac 1 + 150 ℃ temperature range of A method for producing high-strength and high-toughness steel, characterized by performing a heat treatment in which the residence time is 90 seconds or less. In addition to the steel composition, in mass%, Ti: 0.005 to 0.20%
Cu: 0.01 to 2.0%
Ni: 0.01-4.0%
Cr: 0.01 to 2.0%
Mo: 0.01 to 2.0%
Nb: 0.003 to 0.1%
V: 0.003-0.5%
B: 0.0005 to 0.0040%
Ca: 0.0001 to 0.0060%
Mg: 0.0001 to 0.0060%
REM: 0.0001 to 0.0200%
1 or 2 types or more of these are contained, The manufacturing method of the high strength and high toughness steel of Claim 1 characterized by the above-mentioned. The method for producing high-strength and high-toughness steel according to claim 1 or 2, wherein the heat treatment performed after quenching is accelerated and cooled at least in a temperature range from the Ac ₁ transformation point to 600 ° C or lower after heating and holding. The method for producing a high-strength and high-toughness steel according to claim 3, further comprising tempering after accelerated cooling. The method for producing high-strength and high-toughness steel according to any one of claims 1 to 4, wherein the period from the cooling stop during quenching to the start of reheating is continuously performed within 180 seconds.