Low carbon microalloyed steel

Abstract

A low carbon microalloyed steel, comprising in weight % about: 0.05-0.30 C; 0.5-1.5 Mn; 0.04 max S; 0.025 max P; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0-2.0 Cu; up to 0.0250 N; up to 0.2 Cb; up to 0.3 Cr; up to about 0.15 Mo; up to about 0.05 Al; balance Fe and minor additions and impurities. The steel has a carbon equivalent value, C.E., ranging between 0.3-0.65, calculated by the formula: C.E.=C+Mn+Si+Cu+Ni+Cr+Mo+V+Cb 6 15 5

Description

BACKGROUND OF THE INVENTION

The present invention relates generally to the metallurgy of steel and, more particularly, to low carbon microalloyed steel compositions. It is common practice to use conventional microalloyed steels in various applications for bars and tubular products. However, there are needs for stronger and tougher microalloyed steels in a number of different applications such as, for example, in communication towers and hub assemblies.

SUMMARY OF THE INVENTION

The steels of the present invention are much more weldable and tougher than conventional microalloyed steels. The present invention is directed to an alloy broadly comprising in wt. %, about 0.05-0.30 C; up to 1.5 Mn; 1.0 max Si; 0.5-2 Ni; 0.05-0.3 V; up to 2 Cu; 10-250 ppm N; balance Fe and other minor additions and impurities.

BRIEF DESCRIPTION OF THE DRAWING

FIG. 1 is a graph schematically showing the relationship between the precipitation strengthening factor (ΔYS_p) and the Ar₃ temperature in the steels of the present invention.

DETAILED DESCRIPTION OF THE INVENTION

The family of microalloyed steels of the present invention provide better weldability and much higher impact toughness and tensile ductility than conventional microalloyed steels. A critical factor in the design of microalloyed ferrite pearlite steels is the extent to which precipitation strengthening supplements the base strength provided by solid solution and grain refinement. It is known that this precipitation strengthening factor, referred to as ΔYS_p, is controlled by the ferrite transformation temperature, Ar₃, all other things being equal. As the Ar₃ temperature is lowered, ΔYS_p increases up to a maximum and then decreases as a result of precipitation suppression through the usual kinetic limitations at lower temperatures. This relationship is graphically depicted in FIG. 1. The essential design factor for high strength involving precipitation is to adjust Ar₃ by compositional means to allow this maximum to be obtained. Either under (lean) or over (rich) adjustment of the chemistry of the alloy may lead to underutilization of precipitation. Accordingly, two factors must be considered in order to optimize the precipitation according to the invention. The first factor is whether the base composition is too close to the critical limit for formation of bainite such that any further increase in either Mn or Ni (both lower the Ar₃ temperature) causes unwanted bainite formation. The second factor is that for a given Ar₃ temperature, Mn is less potent than Ni in that it suppresses precipitation. Thus, the invention requires the Mn levels to be below 1.5 wt. % and that the Ar₃ temperature be controlled with elements which have a low tendency for forming bainite.

Consideration of these requirements shows that out of all the common alloying elements, Ni is the most effective. The results of a study to examine the effect of Ni on ΔYS_p showed that 45 ksi minimum yield strength and as high as 80 ksi was possible for large bars or tubular products. The results are given in the following tables.

One presently preferred alloy composition according to the present invention contains in % by weight: 0.05-0.30 C, 0.5-1.5 Mn; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0-2.0 Cu; 0.0050-0.0250 N; balance Fe and other minor additions and impurities. The S level is 0.04 wt. % max and preferably about 0.035 wt. % max. The P content is 0.025 wt. % max and preferably about 0.02 wt. % max. In the above composition, the C and N contents may preferably be 0.05-0.15 wt. % C and 0.0010-0.0250 wt. % N.

A further presently preferred embodiment of the present invention includes the alloy composition set forth above, also containing about 0.25-2.0 wt. % Cu. Copper in these microalloyed steels will form as E-copper particles by both interphase precipitation and the normal nucleation and growth process, thus increasing strength by increasing ΔYS_p, and maintaining high levels of toughness and tensile ductility as seen in Tables III and IV.

The alloy may also contain additional constituents such as Cr, Mo, Cb and Al, for example, 0.05-0.3 Cr, up to about 0.15 Mo, up to about 0.2 Cb, up to about 0.05 Al, and more preferably about 0.01-0.03 Al.

TABLE I
Chemical Compositions
Heat
No.	C	Mn	P	S	Si	Cr	Ni	Mo	Cu	Al	V	N(ppm)	C.E.*
2032	0.08	0.52	0.005	0.004	0.25	0.12	1.03	0.03	0.01	0.022	0.144	103	0.34
2033	0.14	0.53	0.004	0.004	0.26	0.12	1.03	0.03	0.01	0.026	0.146	106	0.40
2034	0.07	0.52	0.004	0.004	0.27	0.11	1.03	0.03	0.01	0.026	0.152	20	0.33
2035	0.13	0.52	0.004	0.004	0.26	0.11	1.05	0.03	0.01	0.026	0.138	20	0.39
2036	0.07	0.98	0.005	0.004	0.25	0.11	1.04	0.03	0.01	0.021	0.143	107	0.40
2037	0.14	1.02	0.005	0.004	0.26	0.12	1.03	0.03	0.01	0.024	0.140	112	0.48
2057	0.06	1.03	0.004	0.005	0.26	0.12	1.03	0.03	0.01	0.025	0.146	174	0.40
2058	0.11	1.04	0.004	0.005	0.28	0.12	1.04	0.04	0.01	0.017	0.150	164	0.46
2059	0.08	1.06	0.004	0.005	0.26	0.12	1.54	0.03	0.01	0.023	0.131	186	0.46
2060	0.13	1.03	0.004	0.005	0.25	0.12	1.52	0.03	0.01	0.023	0.148	187	0.51
2061	0.07	1.03	0.004	0.005	0.27	0.12	1.04	0.03	0.01	0.024	0.249	184	0.44
2062	0.12	1.03	0.004	0.005	0.26	0.12	1.03	0.03	0.01	0.029	0.250	176	0.48
2063	0.08	1.02	0.004	0.006	0.26	0.12	1.03	0.03	0.50	0.025	0.152	180	0.46
2135	0.16	1.04	0.004	0.004	0.26	0.14	1.5	0.03	0.01	0.028	0.138	166	0.54
2136	0.26	1.00	0.003	0.004	0.26	0.13	1.5	0.03	0.01	0.028	0.137	170	0.63
2137	0.19	1.00	0.004	0.004	0.26	0.14	0.98	0.03	0.01	0.025	0.227	168	0.55
2138	0.28	1.00	0.004	0.003	0.26	0.14	0.96	0.03	0.01	0.028	0.218	156	0.63
$*C.E.=C+\frac{\mathrm{Mn}+\mathrm{Si}}{6}+\frac{\mathrm{Cu}+\mathrm{Ni}}{15}+\frac{\mathrm{Cr}+\mathrm{Mo}+V+\mathrm{Cb}}{5}$

TABLE II
Rolling Schedule
(1) All billets had a 2250° F. soak
(2) Rolling Sequence:
    Pass No. Reduction (Inches)
    1        2.625-2.000
    2        2.000-1.750
    3        1.750-1.500
    4        1.500-1.250
    5        1.25-1.000
    6        Cross Roll to Straighten Plate (No reduction)
(3) Finish Rolling Temperature (approximately 1950° F. to 2000° F.)
(4) No designation after heat number: Air cooled
    “S” designation after heat number: Sand cooled to simulate the
    mid-radius position of a 6-inch bar

TABLE III
Tensile Properties and Hardness
		Ultimate
	Yield Strength	Tensile	Elongation	R.A.	Hardness
Heat No.	(0.2% offset) (ksi)	Strength (ksi)	(Percent in 1.4″)	(Percent)	(RB)
2032	54.6	70.3	32.0	77.1	81
2032 S	47.7	64.6	32.7	74.7	74
2033	61.3	80.8	28.9	70.6	87
2033 S	51.4	73.1	28.6	67.4	81
2034	50.2	68.3	31.1	76.9	80
2034 S	46.4	65.2	33.1	77.5	74
2035	56.4	79.2	27.8	71.1	86
2035 S	48.2	70.3	30.4	69.7	79
2036	61.9	79.7	28.2	77.1	87
2036 S	52.2	74.3	28.9	77.2	82
2037	70.3	90.8	28.4	72.1	92
2037 S	62.3	83.6	29.9	70.6	88
2057	64.8	84.9	28.0	75.8	91
2057 S	56.8	76.0	30.5	74.4	85
2058	68.3	87.4	28.4	74.2	92
2058 S	60.1	80.6	28.4	73.7	87
2059	71.0	95.1	26.1	72.9	95
2059 S	66.4	87.0	27.8	74.0	92
2060	75.6	101.6	24.4	68.3	98
2060 S	70.3	95.6	24.1	67.2	95
2061	69.8	90.6	26.2	75.3	94
2061 S	60.8	79.6	27.1	75.6	88
2062	74.8	100.2	23.8	65.5	97
2062 S	67.4	90.4	24.2	65.7	94
2063	70.8	90.8	26.6	71.8	93
2063 S	65.5	84.8	28.1	72.6	90
2135	80.3	109.7	23.5	67.9	98
2135 S	72.7	100.2	25.1	67.3	94
2136	89.2	129.2	20.3	53.7	103
2136 S	82.6	116.4	21.2	55.8	99
2137	89.2	118.3	21	54.7	100
2137 S	74.3	103.5	22.6	57.3	96
2138	103	136.7	15.9	39.5	104
2138 S	82.7	117.8	17.9	47.6	100

TABLE IV
Impact Toughness
Charpy V-notch Impact Toughness (ft-lbs)
Test Temperature
	Heat No.	+40° F.	0° F.	−20° F.	−60° F.
	2031	264.0	106.0	9.5	5.0
		—	13.0	11.0	—
	2032 S	—	262.0	20.0	8.0
		—	260.0	113.0	7.5
	2033	79.5	10.5	10.5	—
		15.5	25.5	5.0	—
	2033 S	81.0	26.5	9.0	—
		102.0	51.5	11.0	—
	2034	270.0	7.0	6.5	3.0
		—	—	5.5	—
	2034 S	266.0	12.5	6.0	3.5
		—	8.0	9.0	—
	2035	14.5	9.0	8.0	—
		9.0	12.0	3.5	—
	2035 S	10.0	9.0	5.5	—
		31.0	8.5	6.0	—
	2036	97.5	7.0	10.0	—
		222.0	112.0	6.0	—
	2036 S	—	280.0	160.0	4.0
		—	—	8.0	9.5
	2037	68.5	57.5	44.0	—
		92.5	37.0	56.5	—
	2037 S	110.0	81.5	91.5	—
		121.0	90.0	70.0	—
	2057	84.5	107.5	7.5	5.0
		—	108.0	53.0	23.0
	2057 S	219.0	153.0	124.0	2.5
		—	—	77.5	53.0
	2058	112.0	84.5	53.5	9.5
		—	57.0	43.0	16.0
	2058 S	144.0	95.0	104.0	41.5
		—	102.5	75.5	6.0
	2059	59.0	6.5	26.5	4.0
		—	—	41.0	3.0
	2059 S	107.0	88.5	49.5	9.5
		—	81.0	51.5	7.0
	2060	32.5	8.5	6.0	2.0
		—	29.5	6.0	4.5
	2061	45.5	24.5	24.5	5.0
		—	14.5	6.0	8.0
	2061 S	125.0	103.5	60.0	6.0
		—	92.0	19.0	8.5
	2062	11.0	11.0	12.0	3.5
		—	25.0	10.5	3.5
	2062 S	26.0	7.5	2.5	3.0
		—	37.0	5.0	11.5
	2063	63.0	16.5	18.0	22.5
		—	17.5	16.0	7.5
	2063 S	127.0	115.0	74.5	57.5
		—	76.5	52.5	7.5
Heat No.	+250° F.	+205° F.	+150° F.	+68° F.	+32° F.
2135	—	75.5	48.5	24.5	19.0
	—	—	66.0	18.5	7.0
	—	—	—	30.5	—
2135 S	—	94.5	74.5	51.5	52.5
	—	—	83.0	43.0	34.0
	—	—	—	60.0	—
2136	48.0	28.0	24.0	12.5	—
	—	21.5	20.0	8.0	—
	—	—	—	15.0	—
2136 S	57.0	37.5	27.5	20.0	—
	—	39.0	24.5	20.5	—
	—	—	—	18.5	—
2137	49.5	28.5	25.5	6.0	—
	—	31.5	18.0	10.0	—
	—	—	—	13.5	—
2137 S	49.5	55.5	37.0	26.0	—
	—	36.0	42.5	11.5	—
	—	—	—	19.0	—
2138	20.5	18.5	12.0	7.0	—
	23.0	13.5	14.0	10.0	—
	20.0	—	—	8.0	—
2138 S	36.5	24.5	20.5	5.0	—
	31.5	24.0	21.0	9.5	—
	—	—	—	8.0	—

The “C.E.” or carbon equivalent values reported in Table I may broadly range between 0.3 and 0.65 but, more preferably, are controlled within a range of 0.3 to 0.55 and, still more preferably, controlled within a range of 0.4-0.5 to ensure superior physical properties. The C.E. value of an alloy is calculated using the following formula: $C.E.=C+\frac{\mathrm{Mn}+\mathrm{Si}}{6}+\frac{\mathrm{Cu}+\mathrm{Ni}}{15}+\frac{\mathrm{Cr}+\mathrm{Mo}+V+\mathrm{Cb}}{5}$ Various alloy compositions of the present invention are set forth in Table I which also includes the calculated C.E. values for each. Table II describes the rolling schedule for each of the steel alloy heats made from the compositions of Table I. It will be noted that the billets were either air cooled after completion of rolling or they were sand cooled to simulate the mid-radius position of a large diameter bar of, for example, a 6-inch diameter bar. These sand cooled rolled heats have an “S” designation in Tables III and IV while the rolled heats that, were air cooled have no letter designation in the tables.

While specific embodiments of the invention have been described in detail, it will be appreciated by those skilled in the art that various modifications and alternatives to those details could be developed in light of the overall teachings of the disclosure. The presently preferred embodiments described herein are meant to be illustrative only and not limiting as to the scope of the invention which is to be given the full breadth of the appended claims and any and all equivalents thereof.

Claims

1. A low carbon microalloyed steel, comprising in weight % about: 0.05-0.30 C, 0.5 to less than 1.5 Mn; 0.04 max S; 0.025 max P; 1.0 max Si; 0.5-2.0 Ni; 0.05-0.30 V; 0.01-2.0 Cu; up to 0.0250 N; up to 0.2 Cb; 0.05-0.3 Cr; up to 0.15 Mo; up to 0.05 Al; balance Fe and minor additions and impurities.

2. The steel of claim 1 containing 0.25-2.0 Cu.

3. The steel of claim 1 containing 0.05-0.15 C.

4. The steel of claim 1 containing 0.0010-0.0250 N.

5. The steel composition of claim 1 containing 0.01-0.03 Al.

6. The steel of claim 1 in the form of a bar or tubular shape having a minimum yield strength of 45-80 ksi.

7. The steel of claim 7 haying a minimum yield strength of 65 ksi.

8. The steel of claim 1 having a carbon equivalent value, C.E., ranging between 0.3-0.65, calculated by the formula:

9. A low carbon microalloyed steel having a minimum yield strength of between 45-80 ksi, comprising in weight %: 0.05-0.30 C, 0.5-1.5 Mn; 1.0 max Si; 0.04 max S; 0.025 max P; 0.5-20 Ni; 0.05-0.3 V; 0.01-2.0 Cu; 10-250 ppm N; up to 0.2 Cb; 0.05-0.3 Cr: up to 0.15 Mo; up to 0.05 Al; balance Fe and incidental additions and impurities; and wherein said steel has a carbon equivalent value, C.E., of between about 0.3-0.65, derived from the following formula:

10. The steel of claim 10 wherein the C.E. value is between 0.4-0.5.