CA2033267C - Abrasion resistant steel - Google Patents
Abrasion resistant steelInfo
- Publication number
- CA2033267C CA2033267C CA002033267A CA2033267A CA2033267C CA 2033267 C CA2033267 C CA 2033267C CA 002033267 A CA002033267 A CA 002033267A CA 2033267 A CA2033267 A CA 2033267A CA 2033267 C CA2033267 C CA 2033267C
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- CA
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- Prior art keywords
- steel
- abrasion
- abrasion resistant
- resistant steel
- content
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- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
-
- 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
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
An abrasion resistant steel is provided with approximately 0.05 to 0.45 wt.% C, 0.1 to 1.0 wt.% Si, 0.1 to 2.0 wt.% Mn, 0.05 to 1.5 wt.% Ti and the balance Fe as the basic elements cotributing to the enhancement of the abrasion resistance property without excessively increasing the hardness of the steel, In addition to the basic elements, at least one element selected from the group consisting of 0.1 to 2.0 wt.% Cu, 0.1 to 10.0 wt.% Ni, 0.1 to 3.0 wt;% Cr, 0.1 to 3.0 wt.% Mo and 0.0003 to 0.01 wt.% B may be added to enhance the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0,01 to 0.5 wt:% V may be added to enhance the precipitation hardenability of the steel.
Description
- 203326' TITLE OF THE INVENTION
AN ABRASION RESISTANT STEEL
BACKGROUND OF THE INVENTION
FIELD OF THE INVENTION
The invention relates to the field of metallurgy and particularly relates to the field of an abrasion resistant steel utilized in the field of construction, civil engineering and mining.
DESCRIPTION OF THE RELATED ART
Abrasion resistant steels are utilized in the field of construction) civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the lives of these machines or their parts. It is well known that the steel having high hardness possesses high abrasion resistance property. For this purpose a high alloyed steel treated by quenching has commonly been utilized.
Japanese Patent laid open Publication Nos. 142726 / 19 87) 169359 / 1988 and 142023 / 1989 disclose the information about the production of the conventional abrasion resistant steel. In these inventions the Brinell Hardness of the steel is more than 300. The improvements are aimed at the weldability, the toughness and the workability in bending, and the abrasion resistance property is realized by increasing the hardness of the steel.
However the property required for the abrasion resistant steel has recently become severer and the essential solution to higher abrasion resistance of steel will not be obtained by simply enhancing the hardness of steel. When the hardness of steel is significantly enhanced, the weldability and the workability of steel are deteriorated due to the high alloying and the cost of producing such steels increases significantly.
Accordingly in the practical point of view the significant increase in the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of the steel.
SUMMARY OF THE INVENTION
It is an object of the invention to provide an abrasion resistant steel.
It is an object of the invention to provide an abrasion resistant steel having an excellent abrasion resistance property without considerably increasing the hardness of steel. According to the invention an abrasion resistant steel is provided with approximately 0.05 to 0.45 wt.~ C, 0.1 to 1.0 wt.~ Si, 0.1 to 2.0 wt.~ Mn, 0.05 to 1.5 wt.~ Ti and the balance Fe as the basic elements cotributing to the enhancement of the abrasion resistance property.
In addition to the basic elements, at least one element selected from the group consisting of 0.1 to 2.0 wt.~ Cu, 0.1 to 10.0 wt.~ Ni, 0.1 to 3.0 wt.~ Cr, 0.1 to 3.0 wt.~ Mo and 0.0003 to 0.01 wt.~ B may be added to enhance 2~3326~
the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.~ Nb, 0.01 to 0.5 wt.~ V may be added to enhance the precipitation hardenability of the steel.
A more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.~ in Ti content. A more preferable range with respect to thr balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.~ in Ti content. A more preferable range for stable abrasion resistance is 1.0 to 1.5 wt.~ in Ti content.
A more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.~ in C content. A more Preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.~ in C content. A
more preferable range for stable abrasion resistance of the steel is 0.35to 0.45 wt.~ in C content.
BRIEF DESCRIPTION OF THE DRAWING
Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
DESCRIPTION OF THE PREFERRED EMBODIMENT
The most significant characteristic of the invented steel is effectively utilizing of very hard TiC. In this invention it is not necessary to enhance the hardness 2Q33~6~
of the abrasion resistant steel only by transforming the microstructure of the steel to a martensite which is the conventional way to enhance the abrasion resistance of steel.
In the conventional way the purpose of the addition of titanium to steel is to react with the nitrogen so that the nitrogen is stabilized as TiN. As the result boron does not react with nitrogen since there is not enough nitrogen in the steel, and retained in the steel as a soluble boron, which enhances the quenching hardenability.The quantity of the addition in this case is about 0.02 wt.~ of steel. The addition of a large quantity of titanium to steel is limited by the oxidation of the titanium in the steel melting stage, the clogging of the nozzle and the reaction with the oxidation preventing powder in the casting stage. Therefore the effect of the addition of a large quantity of titanium is not yet known.
The inventors after detailed examination found that the addition of titanium in a large quantity realizes the improvement of steel with respect to the abrasion resistance property.
Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion. The abscissa denotes the added quantity of titanium and the ordinate denotes the ratio of resistance to abrasion.
AN ABRASION RESISTANT STEEL
BACKGROUND OF THE INVENTION
FIELD OF THE INVENTION
The invention relates to the field of metallurgy and particularly relates to the field of an abrasion resistant steel utilized in the field of construction, civil engineering and mining.
DESCRIPTION OF THE RELATED ART
Abrasion resistant steels are utilized in the field of construction) civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the lives of these machines or their parts. It is well known that the steel having high hardness possesses high abrasion resistance property. For this purpose a high alloyed steel treated by quenching has commonly been utilized.
Japanese Patent laid open Publication Nos. 142726 / 19 87) 169359 / 1988 and 142023 / 1989 disclose the information about the production of the conventional abrasion resistant steel. In these inventions the Brinell Hardness of the steel is more than 300. The improvements are aimed at the weldability, the toughness and the workability in bending, and the abrasion resistance property is realized by increasing the hardness of the steel.
However the property required for the abrasion resistant steel has recently become severer and the essential solution to higher abrasion resistance of steel will not be obtained by simply enhancing the hardness of steel. When the hardness of steel is significantly enhanced, the weldability and the workability of steel are deteriorated due to the high alloying and the cost of producing such steels increases significantly.
Accordingly in the practical point of view the significant increase in the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of the steel.
SUMMARY OF THE INVENTION
It is an object of the invention to provide an abrasion resistant steel.
It is an object of the invention to provide an abrasion resistant steel having an excellent abrasion resistance property without considerably increasing the hardness of steel. According to the invention an abrasion resistant steel is provided with approximately 0.05 to 0.45 wt.~ C, 0.1 to 1.0 wt.~ Si, 0.1 to 2.0 wt.~ Mn, 0.05 to 1.5 wt.~ Ti and the balance Fe as the basic elements cotributing to the enhancement of the abrasion resistance property.
In addition to the basic elements, at least one element selected from the group consisting of 0.1 to 2.0 wt.~ Cu, 0.1 to 10.0 wt.~ Ni, 0.1 to 3.0 wt.~ Cr, 0.1 to 3.0 wt.~ Mo and 0.0003 to 0.01 wt.~ B may be added to enhance 2~3326~
the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.~ Nb, 0.01 to 0.5 wt.~ V may be added to enhance the precipitation hardenability of the steel.
A more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.~ in Ti content. A more preferable range with respect to thr balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.~ in Ti content. A more preferable range for stable abrasion resistance is 1.0 to 1.5 wt.~ in Ti content.
A more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.~ in C content. A more Preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.~ in C content. A
more preferable range for stable abrasion resistance of the steel is 0.35to 0.45 wt.~ in C content.
BRIEF DESCRIPTION OF THE DRAWING
Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
DESCRIPTION OF THE PREFERRED EMBODIMENT
The most significant characteristic of the invented steel is effectively utilizing of very hard TiC. In this invention it is not necessary to enhance the hardness 2Q33~6~
of the abrasion resistant steel only by transforming the microstructure of the steel to a martensite which is the conventional way to enhance the abrasion resistance of steel.
In the conventional way the purpose of the addition of titanium to steel is to react with the nitrogen so that the nitrogen is stabilized as TiN. As the result boron does not react with nitrogen since there is not enough nitrogen in the steel, and retained in the steel as a soluble boron, which enhances the quenching hardenability.The quantity of the addition in this case is about 0.02 wt.~ of steel. The addition of a large quantity of titanium to steel is limited by the oxidation of the titanium in the steel melting stage, the clogging of the nozzle and the reaction with the oxidation preventing powder in the casting stage. Therefore the effect of the addition of a large quantity of titanium is not yet known.
The inventors after detailed examination found that the addition of titanium in a large quantity realizes the improvement of steel with respect to the abrasion resistance property.
Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion. The abscissa denotes the added quantity of titanium and the ordinate denotes the ratio of resistance to abrasion.
~0~3~6'~
The ratio of resistance to abrasion is an index wherein the resistance to abrasion of an abrasion resistant steel is devided by that of a mild steel. The resistance to abrasion is measured according to ASTM
Standard G 65-85 wherein an abrasive is introduced between the test specimen and a rotating wheel with a chlorobutyl rubber tire. The abrasive is a sand composed of 100 silica and of controlled size. The C content of the test specimen is 0.3 wt.~ and the specimen is heat treated by quenching. The Brinell Hardness is below 500.
As shown in Figure 1, the ratio of resistance to abrasion linearly increases with the increase of the added quantity of titanium up to 0.5 wt.~. The addition of titanium is effective when the added quantity of titanium is 0.05 wt.~. When the added quantity is 1.5 wt.~) the ratio of resistance to abrasion reaches about 10, which shows the remarkable improvement in the abrasion resistance property.
The followings are the reason why the contents of the elements of the invented steel is specified.
C is an indispensable element in forming TiC and also enhances the hardness of the matrix of steel.
However when C is increased too much, the weldability and the workability are deteriorated. Therefore the upper limit of C is determined to be 0.45 wt.~. As for the lower limit of C the minimum quantity of C wherein the effect of TiC is shown is 0.05 wt.~.
_5_ A more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.~ in C content. A more preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.~ in C content. A
more preferable range for the stable abrasion resistance of the steel is 0.35 to 0.45 wt.~ in C content.
Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.~ is required for this purpose. Si is also an effective element for solution hardening. However when the Si content exceeds 1.0 wt.~, the toughness of steel is lowered and the inclusion in steel is increased. Therefore the Si content is determined to be 0.1 to 1.0 wt.~.
Mn is an element effecive in quenching hardenability. At least 0.1 wt.~ is required for this purpose. When the Mn content exceeds 2.0 wt.~, the weldability of steel is deteriorated. Therefore the Mn content is determined to be 0.1 to 2.0 wt.~.
In this invention Ti is one of the most important element as is C. The addition of at least 0.05 wt.~ of Ti is required to stably form a large quantity of TiC. When the Ti content exceeds 1.5 wt.~, the steel possesses good abrasion resistance property but high cost is required for the production, also the weldability and the workability of steel are lowered. Therefore the Ti content is 203~2(i~
required to be 0.05 to 1.5 wt.~.
A more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.~ in Ti content. A more preferable range with respect to the balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.~ in Ti content. A more preferable range for stable abrasion resistance of the steel is 1.0 to 1.5 wt.~ in Ti content.
In this invention, in addition to the above basic elements) at least one element selected from the group consisting of Cu, Ni, Cr, Mo and B may be added to enhance the quenching hardenability and at least one element selected from the group consisting of Nb and V may be added to enhance the precipitation hardening Cu is an element for enhancing the quenching hardenability and effective in controlling the hardness of steel. When the Cu content is below 0.1 wt.~, the effect is not sufficient. When the Cu content exceeds 2.0 wt.~, the hot workability is lowered and the production cost is increased. Therefore the Cu content is determined to be 0.1 to 2.0 wt.~.
Ni is an element which enhances the quenching hardenability and the low temperature toughness. When the Ni content is below 0.1 wt.~, the effect is not sufficient. When the Ni content exceeds 10.0 wt.~, the production cost is increased significantly.
Therefore the Ni content is determined to be 0.1 to 10.0 _7_ 203326'7 wt.~.
Cr is an element which enhances the quenching hardenability. When the Cr content is below 0.1 wt.~, the effect is not sufficient. When the Cr content exceeds 3.0 wt.~, the weldability is deteriorated) and the production cost is increased. Therefore the Cr content is determined to be 0.1 to 3.0 wt.~.
Mo is an element which enhances the quenching hardenability. When the Mo content is below 0.1 wt.~, the effect is not sufficient. When the Mo content exceeds 3.0 wt.~, the weldability is deteriorated, and the production cost is increased. Therefore the Mo content is determined to be 0.1 to 3.0 wt.~.
B is an element which enhances the quenching hardenability by the addition to steel even by a small amount. When the B content is below 0.0003 wt.~ , the effect is not sufficient. When the B content exceeds 0.01 wt.~, the weldability is deteriorated, and the quenching hardenability is also deteriorated. Therefore the B
content is determined to be 0.0003 to 0.01 wt.~.
Nb is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the Nb content is below 0.005 wt.~, the effect is not sufficient. When the Nb content exceeds 0.5 wt.~) the weldability is deteriorated. Therefore the Nb content is determined to be 0.005 to 0.5 wt.~.
_g_ V is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the V content is below 0.01 wt.~, the effect is not sufficient. When the V
content exceeds 0.5 wt.°6, the weldability is deteriorated.
Therefore the V content is determined to be 0.01 to 0.5 wt. ~.
In this invention no specification is required as for the method of working the steel and as for the method of heat treating of the steel. The invention may not be inoperable by heat treatments such as quenching, annealing) aging and stress relief annealing.
EXAMPLE
Table 1 shows the chemical compositions of the samples of the invented and conventional steel.
Samples from A to 0 are made of the invented steel, whereas samples from P to R are made of the steel for comparison. The chemical composition of the samples from P to R varies with respect to Ti and other alloying elements. The chemical compositions of the samples P
and Q are within the same range with those of the invented steel except that of Ti. The chemical composition of the sample R is within the same range of the invented steel with respect to Ti, but out of the range with respect to C.
_9_ z~3~~6~
Table 1 Kind of C Si Mn Cu Ni Cr Mo Nb V Ti B N
Steel A 0.300.36 0.70- - - - - ~ - 0.09 - 33 B 0.280.37 0.73- - - - - - 0.37 - 38 C 0.290.37 0.74- - - - - - 0.98 - 36 D 0.290.36 0.71- - - - - - 1.41 - 30 E 0.280.36 0.710.24 0.29- - - - 0.40 - 31 F 0.310.33 0.73- - 1.02 0.23 - - 1.08 10 32 G 0.190.33 1.44- - 0.27 - - - 0.65 9 22 H 0.140.34 1.40- - - - 0.025 - 0.40 - 24 I 0.320.34 0.72- - - - - 0.045 0.41 - 21 ,J 0.340.26 1.010.35 0.55- - 0.028 0.041 0.54 - 42 K 0.310.38 0.71- - 0.99 0.23 0.022 0.044 0.06 8 24 L 0.290.38 0.70- - 0.99 0.23 - 0.044 0.08 9 23 M 0.300.36 0.?10.25 - 0.55 0.23 - 0.045 0.19 8 30 N 0.310.36 0.71- - 1.02 0.23 - 0.045 0.38 8 31 0 0.310.33 0.73- 0.360.63 0.34 - - 1.28 - 32 P 0.300.30 0.75- - - - - - 0.02 - 37 Q 0.300.30 0.96- - 1.03 0.21 - 0.045 0.01 11 47 R 0.030.30 0.75- - - - - - 0.47 - 37 Note: The values are in wt.% except B and N. The values of B and N are in ppm.
Table 2.
Process Ratio of Brinell resistance toHardness(HB) A RQ 6.5 474 B - RQ 8.3 393 .. 1 ...R Q.T ~ 4 ........ ..............
. .. 0 0.C '~.... .~....... Z.7 7 ........
.
:
...
C - 1 DQ 9.7 335 ...D Q.T ~ 4 ........6 ..............
0 0'C '~.... . a '..... 2.4 5........
D RQ 9.3 242 E RQ 8.6 390 F RQ 9.1 321 G RQ 4.7 302 H DQ 3.4 253 z RQ 10.1 451 J' DQ 8.9 417 K RQ 6.4 503 L - 1 AR 4.5 293 ..........DQ........................a .............5.~7........
. .......
M 1 AR 4.7 Z86 - 2............. Q ........9 .............4.5 ..M ............... .~........ 4........
..
..
N - 1 AR 6.1 274 ..N..~... ...........RQ....................i.i .............448........
... . 6.......
O - 1 AR 7.3 246 .. .~............... ~ ...... ~.1......... .. 2 O ............... . ........ 7 5"......
.
P RQ 4.9 464 ..........~ ~.........................Z.:..............3 Q - 2 RQ $........ ~ 2 6.,......
~ 5. 2 481 RQ 1.2 122 203320' Table 2 shows the process of making the samples, the ratio of the resistance to abrasion and the Brinell Hardness of the samples. Samples from A to 0 are made of the invented steel, whereas samples from P to R are made of the steel for comparison.
The abrasion test is carried out according to ASTM G
65-85 as decribed before. The measurement of the abrasion is done by the change of the weight of the sample.
As described before the ratio of resistance to abrasion is the ratio of the weight change of the specimen made of the invented steel versus that of the specimen made of a mild steel.
The processes in the table are classified as follows AR, as rolled; RQ) as quenched after heated to 900 °C
following the rolling and air-cooling; RQT) as tempered at the temperature shown in the parenthesis after RQ treatment;
DQ, as directly quenched after finish rolled at 880 °C
following the heating of the slab at 1150 °C ; DQT) as tempered at the temperature shown in the parenthesis following DQ. The thickness of the sample is 15 mm. The kind of steel in Table 1 corresponds with those in Table 2.
The steel for comparison P corresponds with the invented steel A, B-1 and D and the Ti content is below the range of the invented steel. Examining the ratio of the resistance to abrasion, it is found that the ratio is 4.9 in the steel for comparison P, whereas the ratio of the invented steel A is 6.5) that of the steel B-l, 8.3 and that ~Q3326~
of the steel D, 9.3. This is to say that the ratio of the invented steel can be enhanced twice as much as that of the steel for comparison which is a conventional abrasion resistant steel. Moreover the hardness of the invented steel is lower than those of the steel for comparison.
This result agrees with the purpose of the invention wherein the invented steel possesses high resistance to abrasion and low hardness.
The steel for comparison Q corresponds with the invented steel L and N. The ratios of the resistance to abrasion in both L and N are higher than that of Q.
The steel for comparison R corresponds with the invented steel B-1. The C content of the steel for comparison R is below the range of the invented steel.
Since the C content of the steel R is so low that the ratio of the resistance to abrasion is significantly lower than that of B-1.
The ratio of resistance to abrasion is an index wherein the resistance to abrasion of an abrasion resistant steel is devided by that of a mild steel. The resistance to abrasion is measured according to ASTM
Standard G 65-85 wherein an abrasive is introduced between the test specimen and a rotating wheel with a chlorobutyl rubber tire. The abrasive is a sand composed of 100 silica and of controlled size. The C content of the test specimen is 0.3 wt.~ and the specimen is heat treated by quenching. The Brinell Hardness is below 500.
As shown in Figure 1, the ratio of resistance to abrasion linearly increases with the increase of the added quantity of titanium up to 0.5 wt.~. The addition of titanium is effective when the added quantity of titanium is 0.05 wt.~. When the added quantity is 1.5 wt.~) the ratio of resistance to abrasion reaches about 10, which shows the remarkable improvement in the abrasion resistance property.
The followings are the reason why the contents of the elements of the invented steel is specified.
C is an indispensable element in forming TiC and also enhances the hardness of the matrix of steel.
However when C is increased too much, the weldability and the workability are deteriorated. Therefore the upper limit of C is determined to be 0.45 wt.~. As for the lower limit of C the minimum quantity of C wherein the effect of TiC is shown is 0.05 wt.~.
_5_ A more preferable range aiming at the bending workability and the weldability of the steel is 0.05 to 0.2 wt.~ in C content. A more preferable range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance of the steel is 0.2 to 0.35 wt.~ in C content. A
more preferable range for the stable abrasion resistance of the steel is 0.35 to 0.45 wt.~ in C content.
Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.~ is required for this purpose. Si is also an effective element for solution hardening. However when the Si content exceeds 1.0 wt.~, the toughness of steel is lowered and the inclusion in steel is increased. Therefore the Si content is determined to be 0.1 to 1.0 wt.~.
Mn is an element effecive in quenching hardenability. At least 0.1 wt.~ is required for this purpose. When the Mn content exceeds 2.0 wt.~, the weldability of steel is deteriorated. Therefore the Mn content is determined to be 0.1 to 2.0 wt.~.
In this invention Ti is one of the most important element as is C. The addition of at least 0.05 wt.~ of Ti is required to stably form a large quantity of TiC. When the Ti content exceeds 1.5 wt.~, the steel possesses good abrasion resistance property but high cost is required for the production, also the weldability and the workability of steel are lowered. Therefore the Ti content is 203~2(i~
required to be 0.05 to 1.5 wt.~.
A more preferable range aiming at the economy of the steel is 0.05 to 0.3 wt.~ in Ti content. A more preferable range with respect to the balance of the stable abrasion resistance and the economy of the steel is 0.3 to 1.0 wt.~ in Ti content. A more preferable range for stable abrasion resistance of the steel is 1.0 to 1.5 wt.~ in Ti content.
In this invention, in addition to the above basic elements) at least one element selected from the group consisting of Cu, Ni, Cr, Mo and B may be added to enhance the quenching hardenability and at least one element selected from the group consisting of Nb and V may be added to enhance the precipitation hardening Cu is an element for enhancing the quenching hardenability and effective in controlling the hardness of steel. When the Cu content is below 0.1 wt.~, the effect is not sufficient. When the Cu content exceeds 2.0 wt.~, the hot workability is lowered and the production cost is increased. Therefore the Cu content is determined to be 0.1 to 2.0 wt.~.
Ni is an element which enhances the quenching hardenability and the low temperature toughness. When the Ni content is below 0.1 wt.~, the effect is not sufficient. When the Ni content exceeds 10.0 wt.~, the production cost is increased significantly.
Therefore the Ni content is determined to be 0.1 to 10.0 _7_ 203326'7 wt.~.
Cr is an element which enhances the quenching hardenability. When the Cr content is below 0.1 wt.~, the effect is not sufficient. When the Cr content exceeds 3.0 wt.~, the weldability is deteriorated) and the production cost is increased. Therefore the Cr content is determined to be 0.1 to 3.0 wt.~.
Mo is an element which enhances the quenching hardenability. When the Mo content is below 0.1 wt.~, the effect is not sufficient. When the Mo content exceeds 3.0 wt.~, the weldability is deteriorated, and the production cost is increased. Therefore the Mo content is determined to be 0.1 to 3.0 wt.~.
B is an element which enhances the quenching hardenability by the addition to steel even by a small amount. When the B content is below 0.0003 wt.~ , the effect is not sufficient. When the B content exceeds 0.01 wt.~, the weldability is deteriorated, and the quenching hardenability is also deteriorated. Therefore the B
content is determined to be 0.0003 to 0.01 wt.~.
Nb is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the Nb content is below 0.005 wt.~, the effect is not sufficient. When the Nb content exceeds 0.5 wt.~) the weldability is deteriorated. Therefore the Nb content is determined to be 0.005 to 0.5 wt.~.
_g_ V is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the V content is below 0.01 wt.~, the effect is not sufficient. When the V
content exceeds 0.5 wt.°6, the weldability is deteriorated.
Therefore the V content is determined to be 0.01 to 0.5 wt. ~.
In this invention no specification is required as for the method of working the steel and as for the method of heat treating of the steel. The invention may not be inoperable by heat treatments such as quenching, annealing) aging and stress relief annealing.
EXAMPLE
Table 1 shows the chemical compositions of the samples of the invented and conventional steel.
Samples from A to 0 are made of the invented steel, whereas samples from P to R are made of the steel for comparison. The chemical composition of the samples from P to R varies with respect to Ti and other alloying elements. The chemical compositions of the samples P
and Q are within the same range with those of the invented steel except that of Ti. The chemical composition of the sample R is within the same range of the invented steel with respect to Ti, but out of the range with respect to C.
_9_ z~3~~6~
Table 1 Kind of C Si Mn Cu Ni Cr Mo Nb V Ti B N
Steel A 0.300.36 0.70- - - - - ~ - 0.09 - 33 B 0.280.37 0.73- - - - - - 0.37 - 38 C 0.290.37 0.74- - - - - - 0.98 - 36 D 0.290.36 0.71- - - - - - 1.41 - 30 E 0.280.36 0.710.24 0.29- - - - 0.40 - 31 F 0.310.33 0.73- - 1.02 0.23 - - 1.08 10 32 G 0.190.33 1.44- - 0.27 - - - 0.65 9 22 H 0.140.34 1.40- - - - 0.025 - 0.40 - 24 I 0.320.34 0.72- - - - - 0.045 0.41 - 21 ,J 0.340.26 1.010.35 0.55- - 0.028 0.041 0.54 - 42 K 0.310.38 0.71- - 0.99 0.23 0.022 0.044 0.06 8 24 L 0.290.38 0.70- - 0.99 0.23 - 0.044 0.08 9 23 M 0.300.36 0.?10.25 - 0.55 0.23 - 0.045 0.19 8 30 N 0.310.36 0.71- - 1.02 0.23 - 0.045 0.38 8 31 0 0.310.33 0.73- 0.360.63 0.34 - - 1.28 - 32 P 0.300.30 0.75- - - - - - 0.02 - 37 Q 0.300.30 0.96- - 1.03 0.21 - 0.045 0.01 11 47 R 0.030.30 0.75- - - - - - 0.47 - 37 Note: The values are in wt.% except B and N. The values of B and N are in ppm.
Table 2.
Process Ratio of Brinell resistance toHardness(HB) A RQ 6.5 474 B - RQ 8.3 393 .. 1 ...R Q.T ~ 4 ........ ..............
. .. 0 0.C '~.... .~....... Z.7 7 ........
.
:
...
C - 1 DQ 9.7 335 ...D Q.T ~ 4 ........6 ..............
0 0'C '~.... . a '..... 2.4 5........
D RQ 9.3 242 E RQ 8.6 390 F RQ 9.1 321 G RQ 4.7 302 H DQ 3.4 253 z RQ 10.1 451 J' DQ 8.9 417 K RQ 6.4 503 L - 1 AR 4.5 293 ..........DQ........................a .............5.~7........
. .......
M 1 AR 4.7 Z86 - 2............. Q ........9 .............4.5 ..M ............... .~........ 4........
..
..
N - 1 AR 6.1 274 ..N..~... ...........RQ....................i.i .............448........
... . 6.......
O - 1 AR 7.3 246 .. .~............... ~ ...... ~.1......... .. 2 O ............... . ........ 7 5"......
.
P RQ 4.9 464 ..........~ ~.........................Z.:..............3 Q - 2 RQ $........ ~ 2 6.,......
~ 5. 2 481 RQ 1.2 122 203320' Table 2 shows the process of making the samples, the ratio of the resistance to abrasion and the Brinell Hardness of the samples. Samples from A to 0 are made of the invented steel, whereas samples from P to R are made of the steel for comparison.
The abrasion test is carried out according to ASTM G
65-85 as decribed before. The measurement of the abrasion is done by the change of the weight of the sample.
As described before the ratio of resistance to abrasion is the ratio of the weight change of the specimen made of the invented steel versus that of the specimen made of a mild steel.
The processes in the table are classified as follows AR, as rolled; RQ) as quenched after heated to 900 °C
following the rolling and air-cooling; RQT) as tempered at the temperature shown in the parenthesis after RQ treatment;
DQ, as directly quenched after finish rolled at 880 °C
following the heating of the slab at 1150 °C ; DQT) as tempered at the temperature shown in the parenthesis following DQ. The thickness of the sample is 15 mm. The kind of steel in Table 1 corresponds with those in Table 2.
The steel for comparison P corresponds with the invented steel A, B-1 and D and the Ti content is below the range of the invented steel. Examining the ratio of the resistance to abrasion, it is found that the ratio is 4.9 in the steel for comparison P, whereas the ratio of the invented steel A is 6.5) that of the steel B-l, 8.3 and that ~Q3326~
of the steel D, 9.3. This is to say that the ratio of the invented steel can be enhanced twice as much as that of the steel for comparison which is a conventional abrasion resistant steel. Moreover the hardness of the invented steel is lower than those of the steel for comparison.
This result agrees with the purpose of the invention wherein the invented steel possesses high resistance to abrasion and low hardness.
The steel for comparison Q corresponds with the invented steel L and N. The ratios of the resistance to abrasion in both L and N are higher than that of Q.
The steel for comparison R corresponds with the invented steel B-1. The C content of the steel for comparison R is below the range of the invented steel.
Since the C content of the steel R is so low that the ratio of the resistance to abrasion is significantly lower than that of B-1.
Claims (9)
1. An abrasion resistant steel consisting essentially of 0.2 to 0.35 wt.% C, 0.1 to 1 wt.% Si, 0.1 to 2 wt.% Mn, 0.3 to 1 wt.% Ti, 0.0021 to 0.0042 wt.% N, and the balance being Fe and inevitable impurities; and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 245 to 451.
2. The abrasion resistant steel of claim 1, having been prepared by a process comprising hot-rolling, air-cooling, heating and quenching.
3. The abrasion resistant steel of claim 1, having been prepared by a process comprising heating, hot-rolling and direct-quenching.
4. An abrasion resistant steel consisting essentially of 0.2 to 0.35 wt.% C, 0.1 to 1 wt.% Si, 0.1 to 2 wt.% Mn, 0.3 to 1 wt.% Ti, 0.0021 to 0.0042 wt.% N, at least one element selected from the group consisting of 0.1 to 2 wt.%
Cu, 0.1 to 10 wt.% Ni, 0.1 to 3 wt.% Cr, 0.1 to 3 wt.% Mo and 0.0003 to 0.01 wt.% B, and the balance being Fe and inevitable impurities; and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 274 to 448.
Cu, 0.1 to 10 wt.% Ni, 0.1 to 3 wt.% Cr, 0.1 to 3 wt.% Mo and 0.0003 to 0.01 wt.% B, and the balance being Fe and inevitable impurities; and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 274 to 448.
5. The abrasion resistant steel of claim 4, having been prepared by a process comprising hot-rolling, air-cooling, heating and quenching.
6. An abrasion resistant steel consisting essentially of 0.2 to 0.35 wt.% C, 0.1 to 1 wt.% Si, 0.1 to 2 wt.% Mn, 0.3 to 1 wt.% Ti, 0.0021 to 0.0042 wt.% N, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% V, and the balance being Fe and inevitable impurities; and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 274 to 451.
7. An abrasion resistant steel consisting essentially of 0.2 to 0.35 wt.% C, 0.1 to 1 wt.% Si, 0.1 to 2 wt.% Mn, 0.3 to 1 wt.% Ti, 0.0021 to 0.0042 wt.% N, at least one element selected from the group consisting of 0.1 to 2 wt.%
Cu, 0.1 to 10 wt.% Ni, 0.1 to 3 wt.% Cr, 0.1 to 3 wt.% Mo, 0.0003 to 0.01 wt.% B, 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% V, and the balance being Fe and inevitable impurities;
and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 274 to 451.
Cu, 0.1 to 10 wt.% Ni, 0.1 to 3 wt.% Cr, 0.1 to 3 wt.% Mo, 0.0003 to 0.01 wt.% B, 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% V, and the balance being Fe and inevitable impurities;
and the abrasion resistant steel containing TiC and having a ratio of resistance to abrasion in the range from 6.1 to 11.6 when measured according to ASTM standard G65-85 and having a Brinell Hardness in the range from 274 to 451.
8. The abrasion resistant steel of claim 7, having been prepared by a process comprising hot-rolling, air-cooling, heating and quenching.
9. The abrasion resistant steel of claim 7, having been prepared by a process comprising heating, hot-rolling, and direct-quenching.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP148400/90 | 1990-06-06 | ||
| JP14840090 | 1990-06-06 | ||
| JP2148399A JPH0441616A (en) | 1990-06-06 | 1990-06-06 | Production of low-hardness water-resistant steel excellent in wear resistance and bendability |
| EP95120542A EP0714990A1 (en) | 1990-06-06 | 1991-08-12 | Method for making an abrasion resistant steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2033267A1 CA2033267A1 (en) | 1991-12-07 |
| CA2033267C true CA2033267C (en) | 1999-08-24 |
Family
ID=40276095
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002033222A Abandoned CA2033222A1 (en) | 1990-06-06 | 1990-12-27 | Method of making an abrasion resistant steel |
| CA002033267A Expired - Lifetime CA2033267C (en) | 1990-06-06 | 1990-12-27 | Abrasion resistant steel |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002033222A Abandoned CA2033222A1 (en) | 1990-06-06 | 1990-12-27 | Method of making an abrasion resistant steel |
Country Status (6)
| Country | Link |
|---|---|
| EP (2) | EP0527277B1 (en) |
| JP (1) | JPH0441616A (en) |
| AU (4) | AU632187B2 (en) |
| CA (2) | CA2033222A1 (en) |
| FI (2) | FI101403B (en) |
| GB (2) | GB2244718A (en) |
Families Citing this family (23)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0441616A (en) * | 1990-06-06 | 1992-02-12 | Nkk Corp | Production of low-hardness water-resistant steel excellent in wear resistance and bendability |
| US5403410A (en) * | 1990-06-06 | 1995-04-04 | Nkk Corporation | Abrasion-resistant steel |
| US5236521A (en) * | 1990-06-06 | 1993-08-17 | Nkk Corporation | Abrasion resistant steel |
| US5393358A (en) * | 1990-12-03 | 1995-02-28 | Nkk Corporation | Method for producing abrasion-resistant steel having excellent surface property |
| JPH05239591A (en) * | 1992-02-27 | 1993-09-17 | Nkk Corp | Steel excellent in wear resistance |
| US5292384A (en) * | 1992-07-17 | 1994-03-08 | Martin Marietta Energy Systems, Inc. | Cr-W-V bainitic/ferritic steel with improved strength and toughness and method of making |
| US5409554A (en) * | 1993-09-15 | 1995-04-25 | The Timken Company | Prevention of particle embrittlement in grain-refined, high-strength steels |
| US5827379A (en) * | 1993-10-27 | 1998-10-27 | Nippon Steel Corporation | Process for producing extra high tensile steel having excellent stress corrosion cracking resistance |
| KR0153482B1 (en) * | 1994-08-16 | 1998-11-16 | 코오타니 토모카쭈 | Manufacturing method of track link |
| RU2179196C2 (en) * | 1999-12-28 | 2002-02-10 | ОАО "Северсталь" | Steel |
| RU2180016C1 (en) * | 2001-05-14 | 2002-02-27 | Открытое акционерное общество "Северсталь" | Steel for oil-trunk and gas-main pipelines |
| SE525378C2 (en) * | 2002-01-21 | 2005-02-08 | Sandvik Ab | Elements for striking rock drilling and method for its preparation |
| RU2222630C1 (en) * | 2002-08-21 | 2004-01-27 | ООО "Сорби стил" | Steel for gas and oil pipelines |
| FR2847272B1 (en) * | 2002-11-19 | 2004-12-24 | Usinor | METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET |
| FR2847270B1 (en) * | 2002-11-19 | 2004-12-24 | Usinor | METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET |
| JP5017937B2 (en) * | 2005-12-28 | 2012-09-05 | Ｊｆｅスチール株式会社 | Wear-resistant steel plate with excellent bending workability |
| JP4899874B2 (en) * | 2007-01-12 | 2012-03-21 | Ｊｆｅスチール株式会社 | Wear-resistant steel plate with excellent workability and method for producing the same |
| JP5380892B2 (en) * | 2007-05-29 | 2014-01-08 | Ｊｆｅスチール株式会社 | Wear-resistant steel plate with excellent workability and method for producing the same |
| CN101880831B (en) * | 2010-06-13 | 2012-07-04 | 东北大学 | High-strength-and-toughness low alloy wear resistant steel and manufacturing method thereof |
| KR101271781B1 (en) | 2010-12-23 | 2013-06-07 | 주식회사 포스코 | Steel sheet for oil sands slurry transportation system having excellent wear resistance, corrosion resistance and low temperature toughness, and method for manufacturing the same |
| CN102851612A (en) * | 2011-06-29 | 2013-01-02 | 鞍钢股份有限公司 | Wear-resistant steel and heat treatment method thereof |
| CN103556081B (en) * | 2013-10-30 | 2015-12-30 | 莱芜钢铁集团有限公司 | A kind of wear-resisting excavator bucket teeth steel of high-strength and high ductility and manufacture method thereof |
| CN105779885B (en) * | 2014-12-23 | 2018-03-27 | 上海梅山钢铁股份有限公司 | A kind of wear-resistant hot rolling sheet metal and its manufacture method with excellent machinability |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE917674C (en) * | 1942-09-19 | 1954-09-09 | Rheinische Roehrenwerke Ag | Steel for seals |
| DE861706C (en) * | 1948-10-02 | 1953-01-05 | Gussstahlwerk Bochumer Ver Ag | Steel alloy for tempered locomotive wheel tires |
| CH377540A (en) * | 1956-02-06 | 1964-05-15 | Rheinstahl Huettenwerke Ag | Wheel for rail vehicles and process for its manufacture |
| GB982955A (en) * | 1961-07-22 | 1965-02-10 | Hoerder Huettenunion Ag | The manufacture of articles or parts by cold-working steel |
| NL296774A (en) * | 1962-08-17 | |||
| SU168323A1 (en) * | 1964-02-01 | 1965-02-18 | ||
| DE1483210A1 (en) * | 1965-11-23 | 1969-03-20 | Hoerder Huettenunion Ag | Use of an unalloyed steel with good bending properties in longitudinal and transverse directions |
| GB1176855A (en) * | 1966-12-14 | 1970-01-07 | Nippon Kokan Kk | Improvements in or relating to Non-Shielded Arc Welding |
| DE1803511B2 (en) * | 1967-10-17 | 1971-07-29 | HEAT TREATMENT PROCESS FOR ACHIEVING A BAINITIC STRUCTURE IN A STEEL | |
| PL79948B1 (en) * | 1968-01-31 | 1975-08-30 | Mitsubishi Jukogyo Kabushiki Kaisha | |
| PL79950B1 (en) * | 1968-01-31 | 1975-08-30 | Mitsubishi Jukogyo Kabushiki Kaisha | |
| FR1600122A (en) * | 1968-01-31 | 1970-07-20 | ||
| DE1758507B1 (en) * | 1968-06-15 | 1970-12-10 | Thyssen Roehrenwerke Ag | Use of high-strength manganese-alloyed fine-grain structural steel as a material for welded objects with good low-temperature properties |
| SU271807A1 (en) * | 1969-01-22 | 1970-05-26 | HIGH-STRENGTH ARMATURE STEEL | |
| JPS5215523B1 (en) * | 1970-11-18 | 1977-04-30 | ||
| US3925111A (en) * | 1972-12-31 | 1975-12-09 | Nippon Steel Corp | High tensile strength and steel and method for manufacturing same |
| SU441336A1 (en) * | 1973-05-18 | 1974-08-30 | Катав-Ивановский Литейно-Механический Завод | Structural steel |
| JPS582261B2 (en) * | 1973-06-11 | 1983-01-14 | 新日本製鐵株式会社 | Touhou Teki Dekatsukou Engine Seino SI |
| US4472208A (en) * | 1982-06-28 | 1984-09-18 | Sumitomo Metal Industries, Ltd. | Hot-rolled high tensile titanium steel plates and production thereof |
| DE3603691A1 (en) * | 1986-02-06 | 1987-08-20 | Hoesch Stahl Ag | AGING-FREE STEEL |
| CA1320110C (en) * | 1988-06-13 | 1993-07-13 | Hiroshi Tamehiro | Process for manufacturing building construction steel having excellent fire resistance and low yield ratio, and construction steel material |
| JPH0441616A (en) * | 1990-06-06 | 1992-02-12 | Nkk Corp | Production of low-hardness water-resistant steel excellent in wear resistance and bendability |
-
1990
- 1990-06-06 JP JP2148399A patent/JPH0441616A/en active Pending
- 1990-12-04 AU AU67720/90A patent/AU632187B2/en not_active Expired
- 1990-12-07 AU AU67838/90A patent/AU6783890A/en not_active Abandoned
- 1990-12-18 GB GB9027351A patent/GB2244718A/en not_active Withdrawn
- 1990-12-24 GB GB9028005A patent/GB2245282A/en not_active Withdrawn
- 1990-12-27 FI FI906406A patent/FI101403B/en not_active IP Right Cessation
- 1990-12-27 FI FI906407A patent/FI93863C/en not_active IP Right Cessation
- 1990-12-27 CA CA002033222A patent/CA2033222A1/en not_active Abandoned
- 1990-12-27 CA CA002033267A patent/CA2033267C/en not_active Expired - Lifetime
-
1991
- 1991-08-12 EP EP91307393A patent/EP0527277B1/en not_active Expired - Lifetime
- 1991-08-12 EP EP91307390A patent/EP0527276B1/en not_active Expired - Lifetime
-
1993
- 1993-01-11 AU AU31112/93A patent/AU3111293A/en not_active Abandoned
-
1995
- 1995-02-21 AU AU13545/95A patent/AU1354595A/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| FI906406A0 (en) | 1990-12-27 |
| EP0527276B1 (en) | 1997-01-15 |
| FI906406L (en) | 1991-12-07 |
| GB9028005D0 (en) | 1991-02-13 |
| GB2245282A (en) | 1992-01-02 |
| FI101403B1 (en) | 1998-06-15 |
| CA2033222A1 (en) | 1991-12-07 |
| FI93863C (en) | 1995-06-12 |
| AU6772090A (en) | 1991-12-12 |
| FI906407A0 (en) | 1990-12-27 |
| AU6783890A (en) | 1991-12-12 |
| GB9027351D0 (en) | 1991-02-06 |
| EP0527277A1 (en) | 1993-02-17 |
| CA2033267A1 (en) | 1991-12-07 |
| AU3111293A (en) | 1993-02-25 |
| AU632187B2 (en) | 1992-12-17 |
| FI101403B (en) | 1998-06-15 |
| FI906407L (en) | 1991-12-07 |
| JPH0441616A (en) | 1992-02-12 |
| EP0527277B1 (en) | 1997-04-23 |
| EP0527276A1 (en) | 1993-02-17 |
| AU1354595A (en) | 1995-05-04 |
| GB2244718A (en) | 1991-12-11 |
| FI93863B (en) | 1995-02-28 |
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