CA2033222A1 - Method of making an abrasion resistant steel - Google Patents
Method of making an abrasion resistant steelInfo
- Publication number
- CA2033222A1 CA2033222A1 CA002033222A CA2033222A CA2033222A1 CA 2033222 A1 CA2033222 A1 CA 2033222A1 CA 002033222 A CA002033222 A CA 002033222A CA 2033222 A CA2033222 A CA 2033222A CA 2033222 A1 CA2033222 A1 CA 2033222A1
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- Prior art keywords
- abrasion resistant
- resistant steel
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- steel
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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
-
- 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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- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical 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
ABSTRACT OF THE DISCLOSURE
The invention provides a method of making an abrasion resistant steel consisting of the steps of: heating a slab having a chemical composition of about 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 to 1000 to 1300 °C, hot rolling a slab into a hot rolled product of which finishing temperature is the Ar3 point to 1000 °C and directly quenching the hot rolled product, or air cooling and reheating above the Ac3 point followed by quenching the hot rolled product, or air cooling the hot rolled product, or directly quenching and tempering the hot rolled product at below the Ac1 point, air cooling and reheating the hot rolled product at above the Ac3 point followed by quenching and tempering the hot rolled product at below the Ac1 point.
The invention provides a method of making an abrasion resistant steel consisting of the steps of: heating a slab having a chemical composition of about 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 to 1000 to 1300 °C, hot rolling a slab into a hot rolled product of which finishing temperature is the Ar3 point to 1000 °C and directly quenching the hot rolled product, or air cooling and reheating above the Ac3 point followed by quenching the hot rolled product, or air cooling the hot rolled product, or directly quenching and tempering the hot rolled product at below the Ac1 point, air cooling and reheating the hot rolled product at above the Ac3 point followed by quenching and tempering the hot rolled product at below the Ac1 point.
Description
METHOD OF MAKING 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 a method of making 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 hi~h hardness possesses high abrasion resistance property.
For this purpose a high alloyed steel treated by quenching has commonly been utilized. The maximum value of the Brinell Hardness of such abrasion resistant steel in practical use is about 500. There are some other steels which have the Brinell Hardness higher than 500 to further enhance the abrasion resistance property.
However in the above-mentioned abrasion resistant steel the workability of the steel such as the bending workability may be required. To enhance the bending workabilitY it is effective to lower the hardness of steel. As the result, in this kind of steel, the most important characteristic of the abrasion resistant steel, that is, the abrasion resistance property may be deteriorated.
Japanese Patent laid open Publication Nos. 142726 /1987 , 169359 /1988 and 142023 /1989 disclose the information about the production of the conventional abrasion resistant steel.
In these inventions the Brinell Hardness of steel is more than 300. These inventions aim at the improvements in the weldability, the toughness and the workability in bending of steel. However the abrasion resistance property is realized by increasing the hardness of steel.
The property required for the abrasion resistant steel has recently become severer and the essential solution to higherabrasion resistance of steel may 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 of the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of steel.
Summarizing the above-mentioned facts in the conventional abrasion resistant steel, the followings are the points of problems.
(1) The abrasion resistance property of steel is improved by increasing the hardness of steel. Therefore it is necessary to increase the hardness to obtain the abrasion resistance.
However in the steels having high hardness the workability of the steel such as that in bending becomes difficult and the working may cause defects such as crack during the working operation.
Background of the Invention Field of the Invention The invention relates to the field of metallurgy and particularly relates to the field of a method of making 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 hi~h hardness possesses high abrasion resistance property.
For this purpose a high alloyed steel treated by quenching has commonly been utilized. The maximum value of the Brinell Hardness of such abrasion resistant steel in practical use is about 500. There are some other steels which have the Brinell Hardness higher than 500 to further enhance the abrasion resistance property.
However in the above-mentioned abrasion resistant steel the workability of the steel such as the bending workability may be required. To enhance the bending workabilitY it is effective to lower the hardness of steel. As the result, in this kind of steel, the most important characteristic of the abrasion resistant steel, that is, the abrasion resistance property may be deteriorated.
Japanese Patent laid open Publication Nos. 142726 /1987 , 169359 /1988 and 142023 /1989 disclose the information about the production of the conventional abrasion resistant steel.
In these inventions the Brinell Hardness of steel is more than 300. These inventions aim at the improvements in the weldability, the toughness and the workability in bending of steel. However the abrasion resistance property is realized by increasing the hardness of steel.
The property required for the abrasion resistant steel has recently become severer and the essential solution to higherabrasion resistance of steel may 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 of the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of steel.
Summarizing the above-mentioned facts in the conventional abrasion resistant steel, the followings are the points of problems.
(1) The abrasion resistance property of steel is improved by increasing the hardness of steel. Therefore it is necessary to increase the hardness to obtain the abrasion resistance.
However in the steels having high hardness the workability of the steel such as that in bending becomes difficult and the working may cause defects such as crack during the working operation.
(2) To enahance the hardness of steel, the carbon content of steel has to be increased and the alloying elements such as chromium and molybdenum have to be added to the steel. As the result the production cost is increased and the weldability and gas cutting property of steel are considerably deteriorated.
Japanese Patent laid open Publication No. 142726/1987 discloses that the weldability of steel is improved by controlling the carbon content of steel to a lower level.
However the hardness of the steel is at most the level of 400 in Brinell Hardness. Therefore the steel has the practical weldability but the hardness of the steel is limited which gives rise to tbe low abrasion-resistance property under severe abrasion atmosphere.
Japanese Patent laid open Publication No. 169359/ 1988 suggests the abrasion resistant steel having the improved toughness. However the point of the invention is in the improvement of the toughness of steel and the hardness of steel is 400 in Brinell Hardness which is insufficient as the abrasion resistance property under severe abrasion condition.
Japanese Patent laid open Publication No.142023/ 1989 discloses that the bending workability may be improved by the reduction of the quantity of the inclusion in steel and the restriction of the process of making the steel. However 2~33222 the bending workability is improved only by limiting the hardness of steel under 400 in Brinell Hardness.
In short, in the conventional engineering the abrasion resistance property of steel is sacrificed in satisfying the requirement of the workability, the weldabilitY and the toughness of steel.
Summary of the Invention It is an obiect of the invention to provide a method of making an abrasion resistant steel.
It is an object of the invention to provide a method of making an abrasion resistant steel having an excellent abrasion resistance property without deteriorating the workability of steel in bending.
According to the invention a method of making an abrasion resistant steel is provided comprising the steps of:
(a) heating a slab consisting essentially of about 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 having the carbon equivalent C~
specified below of at most 0.20 wt.X to the temperature of 1000 to 1300 C;
C~ = ~ C wt.%~ - ~ Ti wt.% ~ (12/ 48).
where ~ C wt.%~ is the carbon content of said abrasion resistant steel and ~ Ti wt.x ) is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 ~33222 point of the abrasion resistant steel to 1000 C and (c) directly quenching said hot rolled product, or air cooling and reheating the hot rolled product to the temPerature at least the Ac3 point of the abrasion resistant steel followed by quenching the hot rolled product.
Whether the carbon equivalent is prescribed as above or not, the followings are the processes of the hot rolled rolled product having the chemical composition specified above.
(1) air coo]ing the hot rolled product, (2) directly quenching and tempering the hot rolled product at the temperature at most the Ac1 point of the steel, (3) air cooling and reheating the hot rolled product at the temperature at least the Ac3 point of the steel followed by quenching and tempering the hot rolled product at the temperature of at most the Acl point 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.X 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, 0.01 to 0.5 wt.% Y 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 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 the stable abrasion resistance is 1.0 to 1.5 wt.% in Ti content.
Brief Description of the Drawing Figure 1 is a graph showing the relationship between the hardness and the bending workability of steel. Figure 2 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion. Figure 3 is graphes showing the relationship between the Brinell Hardness of steel and the ratio of resistance to abrasion thereof. Figure 4 is graphes showing the relationship between the carbon equivalent and the Brinell Hardness of steel.
Description of the Preferred Embodiment The invention concerns --wi-th a steel having good abrasion resistance and also good bending workability. The important characteristic of the invention is the bending workability.
The hardness of steel has a close relationship with the bending workability thereof. When the hardness is lowered, the bending workability is improved.
Figure 1 is a graph showing the relationship between the hardness and the bending workability of steel. The abscissa denotes Brinell Hardness of steel and the ordinate denotes the critical bending radius. The critical bending radius is the smallest radius of the specimen for bending test wherein no crack is generated on the surface of the specimen. The 2~33222 smaller the critical bending radius the easier for the tested steel to be bent without cracking. The value of the ordinate is the critical radius divided by the thickness of the specimen. Therefore the unit of the ordinate is the thickness of the specimen. The thickness of the specimen is 15 to 25 mm and the width thereof is 150 to 200 mm. In Figure 1 the domain under the curve "a" is the area where the specimen cracks by the test of bending and the domain above the curve "b" is the area where the specimen does not crack, the domain between the curves "a" and "b" being a transional area.
In this invention the target of the maximum critical bending radius is 3.0 in terms of the thickness of the specimen.
To satisfy the given condition the Brinell Hardness of the specimen has to be 401 at most.
According}y the hardness of the invented steel is determined to be at most ~00 in Brinell Hardness. Therefore the domain of the invented steel complying with the above-mentioned requirement is the area encircled by the points A, B, C and D.
The significant characteristic of the invented steel is effectively utilizing of very hard TiC. In this invention it is not necessary to enhance the hardness of the abrasion resistant steel oniy 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 ~3222 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 of steel. The quantity of the addition in this case is about 0.02 wt.% of the 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 2 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. 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 achlorobutyl rubber tire. The abrasive is a sand composed of 100% silica and of controlled size. The C content of test specimen is 0.3 wt.% and the 2~33~2 specimen is heat treated by quenching.
The Brinell Hardness is at most 500. In Figure 2 the area below the curve "c" and above the curve "d" is where the test results of the steel is distributed. As shown in Figure ~, 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.
Figure 3 is graphes showing the relationship between the Brinell Hardness of steel and the ratio of resistance to abrasion thereof. The abscissa denotes the Brinell Hardenes and the ordinate denotes the ratio of resistance to abrasion.
The area below the curve-- "f" and above the curve "g " is where the test results of the conventional steel having the Ti content of at most 0.05 wt.X are distributed. In the area on the right hand side of the line "e" , wherein the Brinell Hardness is 401. and above the curve "f" , the test results of the conventional steel having Ti content of 0.05 to 0.15 is distributed. In the area on the left side of the line "e" the test results of the invented steel having Ti content of 0.05 to 0.15 is distributed, being encircled by the dotted curve "h" . Even if the ratio of resistance to abrasion is in the same range with that of the conventional steel, the Brinell Hardness of the invented steel is ~33222 significantiy lower than that of the conventional steel.
As mentioned above the invented steel satisfy the requirement of the bending workability without sacrificing the resistance to abrasion. The invented steel solves the problem by the precipitation and the dispersion of TiC in steel.
Thus the invented steel satisfies the limitation of the bending workability by limiting the Brinell Hardness to at most 400, and still retains the resistance to abrasion due mainly to the precipitated TiC.
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 O.45 wt.%. - As for the lower Jimit of C
the minimum quantity of C wherein the effect of TiC is shown is 0.05 wt.%.
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. ~owever 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 effective in quenching hardenability.
At least 0.1 wt.% is required for this purpose. When the 2~33222 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 elements 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 productioD, also the weldability and the workability of steel are lowered. Therefore the Ti content is determined 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 the stable abrasion resistance 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.%, 2~33222 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.
WheD 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 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 O.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 2~33222 be 0.0003 to 0.01 wt.%.
Nb is an element effective in the precipitation hardening and can controi 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.%.
Y 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.%, the weldability is deteriorated. Therefore the V
content is determined to be 0.01 to 0.5 wt.X.
The method of making, or working and heat treating of the invented steel is explained below.
The slabs having the chemical composition described above are heated to the temperature of 1000 to 1300 C, and hot rolled. The finishing temperature of the rolling is from the Ar3 point to 1000 C.
In this invention an excellent abrasion resistance property is obtained when TiC is stabilized. Therefore the heating temperature is desirable to be below the temperature wherein TiC is dissolved into steel, which is considerably high. However in practical point of view the upper limit of the heating temperature is determined to be 1300 C
considering the heating cost. The lower limit of the heating temperature is determined to be 1000 C considering the rolling 20~3222 efficiency.
When the finishing temperature is below the Ar3 point, the hardeness of steel is significantly lowered since the ferrite is generated in the steel.
Therefore the lower limit of the finishing temperature is determined to be the Ar3 point. The upper limit of the finishing temperature is determined to be 1000C considering the temperature of the heated slabs.
The process after the rolling is classified according to C~ , or the carbon equivalent to limit the Brinell Hardness to at most 401.
The carbon equivalent is defined by the following equation;
C~ = ~ C %~ - ~ Ti %~ X (12/ 48), where ~ C %~ is the C content and ~ Ti %) is the Ti content.
The carbon equivalent almost corresponds with the soluble carbon of steel. ~ When the carbon equivalent is high, so is the hardeness of steel. Therefore in this invention the processes after the rolling are classified according to the carbon equivalent.
Figure 4 is graphes showing the relationship between the carbon equivalent and the Brinell Hardness of steel. The abscissa is the carbon equivalent and the ordinate is the Brinell Hardness of steel. In Figure 4 the open marks denote the invented steel and the solid mark denotes the steel in comparison or the conventional steel. The cirular mark denotes the process RQ or DQ while the triangular mark denotes the processes RQT, DQT and AR. RQ signifies the process wherein the material is air colled after finish rollin~
followed by reheating and quenching. DQ signifies the process wherein the material is directly quenched just after finish rolling. RQT signifies the process wherein the material is tempered after RQ. DQT signifies the process wherein the material is tempered after DQ. AR signifies as rolled. In Figure 4, line "j" signifies the line wherein the Brinell Hardness is 401. The area wherein the data of the invented steel; open circle marks, are generally distributed between the curves "k" and "I" . The area wherein the data of the invented steel; open triangular marks, are generally distributed between the curves "m" and "n" . The area wherein the data of the conventional steel, or steel in comparison; solid circular marks, are generallY distributed between the curves "o" and "p" .
When the carbon equivalent C~ is at most 0.20 wt.%, the Brinell Hardness is at most 401 in spite of the processes after finish rolling. However when the carbon equivalent C~
exceeds 0.20 wt.X, whether the Brinell Hardness of the steel is at most 401, depends on the processes. When the process is DQ or RQ, the Brinell Hardness cf the steel exceeds 401. When the process is DQT or RQT or AR, the BrinelJ
Hardness of the steel is at most 401.
As the result of the aforementioned description the processes after finish rolling are classified as follows by the carbon equivalent.
(1) In case of C~ ~ 0.20 wt.%:
The steel may be treated by the following processes;
directly quenching iust after finish rolling, ~ quenching after the steel is reheated to at least the temperature of the Ac3 point following finish rolling and air cooling.
air cooling after finish rolling, ~ tempering at the temperature of at most the Acl point followed by directly quenching after finish rolling, ~ tempering at the temperature of at most the Acl point followed by quenching after finish rolling and reheating to at least the temperature of Ac3.
In this invention the abrasion resistance is obtained by adding a large quantity of TiC. However the harder the matrix of the steel, the better the abrasion resistance property.
Sufficient hardness is obtained in the processes ~ and . In case of the process ~, the steel is reheated to at least the temperature of the Ac3 point since the structure of the steel is not homogeneously austenitic when the steel is reheated below the temperature of the Ac3 point, whereby the elevation of the hardness is not expected.
The hardness of the steel should be at most 401 in Brinell Hardness in order to obtain the bending workability.
When the carbon equivalent is at most 0.20 wt.%, the hardness of the steel is at most 401 in case of the process of ~ or In case of the process ~3 or ~, the steel is tempered 2~33222 after quenching which gives rise to the lowering of the hardness and enhancing the bending workability. In case of @~ or ~, when the tempering temperature exceeds the Ac~ point, the structure of steel becomes partially austenite. Hence the tempering temperature is determined to be at most the Acl point.
In case of the process ~, the hardenes of steel is low and good abrasion resistance property is obtained.
(2) In case of C* > 0.20 wt.%:
In contrast to the case of C* ~ 0.20 wt.%, the processes are restricted to ~ 3 and ~. In cases of ~ and ~
, the Brinell Hardness exceeds 401, which lowers the bending workability of steel. Therefore the quenched steel having this range of the carbon equivalent needs the tempering process of ~3 and ~ which softens the steel. In the processes and ~, the tempering temperature should be at most Acl since when the steel is tempered at- more than the Ac1 point, the structure of the steel is partially transformed to austenite and the stable quality of steel can not be obtained. In case the process ~, the hardness of the steel is low and good abrasion resistance property is obtained.
In this invention the steel treated by the processes specified above can satisfy the required property even if the steel is further treated by aging or stress relief tempering.
EXAMPLE
Table 1 shows the chemical compositions of the samples 2~33222 of the invented and conventional steel.
Samples from A to O 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 composition 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.
.
2~33222 Table 1 Kind C Si Mn Cu Ni Cr Mo ~b V Ti B N
Steel _ A 0.30 0.36 0.70 . 0.09 33 B 0.28 0.37 0.73 0.37 38 C 0.29 0.37 0.74 0.98 36 D 0.29 0.36 0.71 1.41 30 .,...... ................ ................ ................. ................. ................ ................ ...................... ...................... ...............
....... ...
E 0.28 0.36 0.71 0.24 0.29 . 0.40 31 F 0.31 0.33 P.73 1.02 0.23 1.08 10 32 G 0.19 0.33 1.44 0.27 0.65 9 22 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
.. ...................... ....
H 0.14 0.34 1.40 0.025 0.40 24 I 0.32 0.34 0.72 0.045 0.41 21 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
... ,.... ..
J 0.34 0.26 1.01 0.35 0.55 0.028 0.041 0.54 42 K 0.31 0.38 0.71 0.99 0.23 0.022 0.044 0.06 8 24 L 0.29 0.38 0.70 0.99 0.23 0.044 0.08 9 23 M 0.30 0.36 0.71 0.25 0.55 0.23 0.045 0.19 8 30 N 0.31 0.36 0.71 1.02 0.23 0.045 0.38 8 31 0 0.31 0.33 0.73 0.36 0.63 0.34 1.28 32 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
.. ...................... ....
P 0.30 0.30 0.75 0.02 37 Q 0.30 0.30 0.96 1.03 0.21 0.045 0.01 ll 47 R 0.03 0.30 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 I HB C*
1 B RQ 8.3 393 0.188 2 BRQT (400 ~C ) 6.1 277 0.188 3 C DQ 9. 7 335 0.045 4 CDQT (400 ~C ) 6.8 245 0.045 Invented Steel 5 D RQ 9.3 242 -0.063 6 E RQ 8.6 390 0.180 7 F 321 0.040 8 G RQ 4.7 302 0.028 9 H DQ 3.4 253 0.040 L AR 4.5 293 0.270 11 M AR 4.7 286 0.253 _ 12 N AR 6.1 274 0.215 13 0 AR 7.3 246 -0.010 14 0 RQ 11 .1 275 -0.010 I A RQ 6.5 474 0.278 2 I RQ 10.1 451 0.218 3 J DQ 8.9 417 0.205 Steel 4 K RQ 6.4 503 0.295 in 5 L DQ 8.2 507 0.270 Comparison 6 M RQ 9.1 454 0.253 7 N RQ 11.6 448 0.215 8 P RQ 4.9 464 0.295 9 Q AR 2. 8 326 0.298 Q RQ 5.2 481 0.298 11 R RQ 1.2 122 -0.088 Table 2 shows the process of making the samples, the ratio of the resistance to abrasion, Brinell Hardness and the equivalent carbon of the samples. The alphabetical notations at the left parts of Tables 1 and 2 denote the same kind of steels. The abrasion test is carried out according to ASTM G 65-85 as decribed before. The measllrement 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 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 reheating; RQT, as tempered after RQ treatment; DQ, as directly quenched; DQT, as tempered following DQ.
The kind of steel in Table 1 corresponds with those in Table 2.
The cases-of which numbering are 1 to 1~ on the upper lines, are of the invented steel, and the cases of which numbering are 1 to 11 on the lower lines, are of the conventional steel, or steel in comparison.
Case No. 8 of the steel for comparison corresponds with the cases of invented steel Nos. 1 and 5 but in case No. 8, 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 case No. 8 of the steel for comparison, whereas the ratio of No.1 of the invented steel is 8.3, that of case 5 of the invented ateel is 9.3. This is to say that the ratio of the invented steel can be enhanced about 2~3~22 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 401 in Brinell Hardness.
This result agrees with the purpose of the invention wherein the invented steel treated by the invented process possesses high resistance to abrasion and low hardness.
Case 9 of the steel for comparison corresponds with cases 10 and 12 of the invented steel. The hardness of steel of case 9 of the steel for comparison satisfies the condition wherein the Brinell Hardness is at most 401, but the ratio of resistance to abrasion is lower than in the cases 10 and 12 of the invented steel.
Case 11 of the steel for comparison corresponds with case 1 of the invented steel. However the carbon content of the steel in case 11 of the steel for comparison is below the half of the lower limit of prescription in invented steel.
Therefore the hardness of steel in case 11 of the steel for comparison is sufficiently low but the abrasion resistance is much lower than that of the invented steel.
The chemical composition of the steel in cases Nos. 1 to 7 is in the range of the invented steel and these steels possess the excellent abrasion resistant property. However these samples are as directly quenched or as quenched after reheatihg in spite of the fact wherein the carbon equivalents of these samples exceeds 0.20 wt.%. Accordingly the Brinell Hardness of these samples is above 401, which deteriorates the bending workability of steel.
Japanese Patent laid open Publication No. 142726/1987 discloses that the weldability of steel is improved by controlling the carbon content of steel to a lower level.
However the hardness of the steel is at most the level of 400 in Brinell Hardness. Therefore the steel has the practical weldability but the hardness of the steel is limited which gives rise to tbe low abrasion-resistance property under severe abrasion atmosphere.
Japanese Patent laid open Publication No. 169359/ 1988 suggests the abrasion resistant steel having the improved toughness. However the point of the invention is in the improvement of the toughness of steel and the hardness of steel is 400 in Brinell Hardness which is insufficient as the abrasion resistance property under severe abrasion condition.
Japanese Patent laid open Publication No.142023/ 1989 discloses that the bending workability may be improved by the reduction of the quantity of the inclusion in steel and the restriction of the process of making the steel. However 2~33222 the bending workability is improved only by limiting the hardness of steel under 400 in Brinell Hardness.
In short, in the conventional engineering the abrasion resistance property of steel is sacrificed in satisfying the requirement of the workability, the weldabilitY and the toughness of steel.
Summary of the Invention It is an obiect of the invention to provide a method of making an abrasion resistant steel.
It is an object of the invention to provide a method of making an abrasion resistant steel having an excellent abrasion resistance property without deteriorating the workability of steel in bending.
According to the invention a method of making an abrasion resistant steel is provided comprising the steps of:
(a) heating a slab consisting essentially of about 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 having the carbon equivalent C~
specified below of at most 0.20 wt.X to the temperature of 1000 to 1300 C;
C~ = ~ C wt.%~ - ~ Ti wt.% ~ (12/ 48).
where ~ C wt.%~ is the carbon content of said abrasion resistant steel and ~ Ti wt.x ) is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 ~33222 point of the abrasion resistant steel to 1000 C and (c) directly quenching said hot rolled product, or air cooling and reheating the hot rolled product to the temPerature at least the Ac3 point of the abrasion resistant steel followed by quenching the hot rolled product.
Whether the carbon equivalent is prescribed as above or not, the followings are the processes of the hot rolled rolled product having the chemical composition specified above.
(1) air coo]ing the hot rolled product, (2) directly quenching and tempering the hot rolled product at the temperature at most the Ac1 point of the steel, (3) air cooling and reheating the hot rolled product at the temperature at least the Ac3 point of the steel followed by quenching and tempering the hot rolled product at the temperature of at most the Acl point 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.X 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, 0.01 to 0.5 wt.% Y 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 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 the stable abrasion resistance is 1.0 to 1.5 wt.% in Ti content.
Brief Description of the Drawing Figure 1 is a graph showing the relationship between the hardness and the bending workability of steel. Figure 2 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion. Figure 3 is graphes showing the relationship between the Brinell Hardness of steel and the ratio of resistance to abrasion thereof. Figure 4 is graphes showing the relationship between the carbon equivalent and the Brinell Hardness of steel.
Description of the Preferred Embodiment The invention concerns --wi-th a steel having good abrasion resistance and also good bending workability. The important characteristic of the invention is the bending workability.
The hardness of steel has a close relationship with the bending workability thereof. When the hardness is lowered, the bending workability is improved.
Figure 1 is a graph showing the relationship between the hardness and the bending workability of steel. The abscissa denotes Brinell Hardness of steel and the ordinate denotes the critical bending radius. The critical bending radius is the smallest radius of the specimen for bending test wherein no crack is generated on the surface of the specimen. The 2~33222 smaller the critical bending radius the easier for the tested steel to be bent without cracking. The value of the ordinate is the critical radius divided by the thickness of the specimen. Therefore the unit of the ordinate is the thickness of the specimen. The thickness of the specimen is 15 to 25 mm and the width thereof is 150 to 200 mm. In Figure 1 the domain under the curve "a" is the area where the specimen cracks by the test of bending and the domain above the curve "b" is the area where the specimen does not crack, the domain between the curves "a" and "b" being a transional area.
In this invention the target of the maximum critical bending radius is 3.0 in terms of the thickness of the specimen.
To satisfy the given condition the Brinell Hardness of the specimen has to be 401 at most.
According}y the hardness of the invented steel is determined to be at most ~00 in Brinell Hardness. Therefore the domain of the invented steel complying with the above-mentioned requirement is the area encircled by the points A, B, C and D.
The significant characteristic of the invented steel is effectively utilizing of very hard TiC. In this invention it is not necessary to enhance the hardness of the abrasion resistant steel oniy 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 ~3222 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 of steel. The quantity of the addition in this case is about 0.02 wt.% of the 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 2 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. 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 achlorobutyl rubber tire. The abrasive is a sand composed of 100% silica and of controlled size. The C content of test specimen is 0.3 wt.% and the 2~33~2 specimen is heat treated by quenching.
The Brinell Hardness is at most 500. In Figure 2 the area below the curve "c" and above the curve "d" is where the test results of the steel is distributed. As shown in Figure ~, 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.
Figure 3 is graphes showing the relationship between the Brinell Hardness of steel and the ratio of resistance to abrasion thereof. The abscissa denotes the Brinell Hardenes and the ordinate denotes the ratio of resistance to abrasion.
The area below the curve-- "f" and above the curve "g " is where the test results of the conventional steel having the Ti content of at most 0.05 wt.X are distributed. In the area on the right hand side of the line "e" , wherein the Brinell Hardness is 401. and above the curve "f" , the test results of the conventional steel having Ti content of 0.05 to 0.15 is distributed. In the area on the left side of the line "e" the test results of the invented steel having Ti content of 0.05 to 0.15 is distributed, being encircled by the dotted curve "h" . Even if the ratio of resistance to abrasion is in the same range with that of the conventional steel, the Brinell Hardness of the invented steel is ~33222 significantiy lower than that of the conventional steel.
As mentioned above the invented steel satisfy the requirement of the bending workability without sacrificing the resistance to abrasion. The invented steel solves the problem by the precipitation and the dispersion of TiC in steel.
Thus the invented steel satisfies the limitation of the bending workability by limiting the Brinell Hardness to at most 400, and still retains the resistance to abrasion due mainly to the precipitated TiC.
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 O.45 wt.%. - As for the lower Jimit of C
the minimum quantity of C wherein the effect of TiC is shown is 0.05 wt.%.
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. ~owever 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 effective in quenching hardenability.
At least 0.1 wt.% is required for this purpose. When the 2~33222 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 elements 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 productioD, also the weldability and the workability of steel are lowered. Therefore the Ti content is determined 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 the stable abrasion resistance 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.%, 2~33222 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.
WheD 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 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 O.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 2~33222 be 0.0003 to 0.01 wt.%.
Nb is an element effective in the precipitation hardening and can controi 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.%.
Y 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.%, the weldability is deteriorated. Therefore the V
content is determined to be 0.01 to 0.5 wt.X.
The method of making, or working and heat treating of the invented steel is explained below.
The slabs having the chemical composition described above are heated to the temperature of 1000 to 1300 C, and hot rolled. The finishing temperature of the rolling is from the Ar3 point to 1000 C.
In this invention an excellent abrasion resistance property is obtained when TiC is stabilized. Therefore the heating temperature is desirable to be below the temperature wherein TiC is dissolved into steel, which is considerably high. However in practical point of view the upper limit of the heating temperature is determined to be 1300 C
considering the heating cost. The lower limit of the heating temperature is determined to be 1000 C considering the rolling 20~3222 efficiency.
When the finishing temperature is below the Ar3 point, the hardeness of steel is significantly lowered since the ferrite is generated in the steel.
Therefore the lower limit of the finishing temperature is determined to be the Ar3 point. The upper limit of the finishing temperature is determined to be 1000C considering the temperature of the heated slabs.
The process after the rolling is classified according to C~ , or the carbon equivalent to limit the Brinell Hardness to at most 401.
The carbon equivalent is defined by the following equation;
C~ = ~ C %~ - ~ Ti %~ X (12/ 48), where ~ C %~ is the C content and ~ Ti %) is the Ti content.
The carbon equivalent almost corresponds with the soluble carbon of steel. ~ When the carbon equivalent is high, so is the hardeness of steel. Therefore in this invention the processes after the rolling are classified according to the carbon equivalent.
Figure 4 is graphes showing the relationship between the carbon equivalent and the Brinell Hardness of steel. The abscissa is the carbon equivalent and the ordinate is the Brinell Hardness of steel. In Figure 4 the open marks denote the invented steel and the solid mark denotes the steel in comparison or the conventional steel. The cirular mark denotes the process RQ or DQ while the triangular mark denotes the processes RQT, DQT and AR. RQ signifies the process wherein the material is air colled after finish rollin~
followed by reheating and quenching. DQ signifies the process wherein the material is directly quenched just after finish rolling. RQT signifies the process wherein the material is tempered after RQ. DQT signifies the process wherein the material is tempered after DQ. AR signifies as rolled. In Figure 4, line "j" signifies the line wherein the Brinell Hardness is 401. The area wherein the data of the invented steel; open circle marks, are generally distributed between the curves "k" and "I" . The area wherein the data of the invented steel; open triangular marks, are generally distributed between the curves "m" and "n" . The area wherein the data of the conventional steel, or steel in comparison; solid circular marks, are generallY distributed between the curves "o" and "p" .
When the carbon equivalent C~ is at most 0.20 wt.%, the Brinell Hardness is at most 401 in spite of the processes after finish rolling. However when the carbon equivalent C~
exceeds 0.20 wt.X, whether the Brinell Hardness of the steel is at most 401, depends on the processes. When the process is DQ or RQ, the Brinell Hardness cf the steel exceeds 401. When the process is DQT or RQT or AR, the BrinelJ
Hardness of the steel is at most 401.
As the result of the aforementioned description the processes after finish rolling are classified as follows by the carbon equivalent.
(1) In case of C~ ~ 0.20 wt.%:
The steel may be treated by the following processes;
directly quenching iust after finish rolling, ~ quenching after the steel is reheated to at least the temperature of the Ac3 point following finish rolling and air cooling.
air cooling after finish rolling, ~ tempering at the temperature of at most the Acl point followed by directly quenching after finish rolling, ~ tempering at the temperature of at most the Acl point followed by quenching after finish rolling and reheating to at least the temperature of Ac3.
In this invention the abrasion resistance is obtained by adding a large quantity of TiC. However the harder the matrix of the steel, the better the abrasion resistance property.
Sufficient hardness is obtained in the processes ~ and . In case of the process ~, the steel is reheated to at least the temperature of the Ac3 point since the structure of the steel is not homogeneously austenitic when the steel is reheated below the temperature of the Ac3 point, whereby the elevation of the hardness is not expected.
The hardness of the steel should be at most 401 in Brinell Hardness in order to obtain the bending workability.
When the carbon equivalent is at most 0.20 wt.%, the hardness of the steel is at most 401 in case of the process of ~ or In case of the process ~3 or ~, the steel is tempered 2~33222 after quenching which gives rise to the lowering of the hardness and enhancing the bending workability. In case of @~ or ~, when the tempering temperature exceeds the Ac~ point, the structure of steel becomes partially austenite. Hence the tempering temperature is determined to be at most the Acl point.
In case of the process ~, the hardenes of steel is low and good abrasion resistance property is obtained.
(2) In case of C* > 0.20 wt.%:
In contrast to the case of C* ~ 0.20 wt.%, the processes are restricted to ~ 3 and ~. In cases of ~ and ~
, the Brinell Hardness exceeds 401, which lowers the bending workability of steel. Therefore the quenched steel having this range of the carbon equivalent needs the tempering process of ~3 and ~ which softens the steel. In the processes and ~, the tempering temperature should be at most Acl since when the steel is tempered at- more than the Ac1 point, the structure of the steel is partially transformed to austenite and the stable quality of steel can not be obtained. In case the process ~, the hardness of the steel is low and good abrasion resistance property is obtained.
In this invention the steel treated by the processes specified above can satisfy the required property even if the steel is further treated by aging or stress relief tempering.
EXAMPLE
Table 1 shows the chemical compositions of the samples 2~33222 of the invented and conventional steel.
Samples from A to O 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 composition 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.
.
2~33222 Table 1 Kind C Si Mn Cu Ni Cr Mo ~b V Ti B N
Steel _ A 0.30 0.36 0.70 . 0.09 33 B 0.28 0.37 0.73 0.37 38 C 0.29 0.37 0.74 0.98 36 D 0.29 0.36 0.71 1.41 30 .,...... ................ ................ ................. ................. ................ ................ ...................... ...................... ...............
....... ...
E 0.28 0.36 0.71 0.24 0.29 . 0.40 31 F 0.31 0.33 P.73 1.02 0.23 1.08 10 32 G 0.19 0.33 1.44 0.27 0.65 9 22 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
.. ...................... ....
H 0.14 0.34 1.40 0.025 0.40 24 I 0.32 0.34 0.72 0.045 0.41 21 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
... ,.... ..
J 0.34 0.26 1.01 0.35 0.55 0.028 0.041 0.54 42 K 0.31 0.38 0.71 0.99 0.23 0.022 0.044 0.06 8 24 L 0.29 0.38 0.70 0.99 0.23 0.044 0.08 9 23 M 0.30 0.36 0.71 0.25 0.55 0.23 0.045 0.19 8 30 N 0.31 0.36 0.71 1.02 0.23 0.045 0.38 8 31 0 0.31 0.33 0.73 0.36 0.63 0.34 1.28 32 ...................... ................ ................ ................. ................ ................ ................ ...................... ....................
.. ...................... ....
P 0.30 0.30 0.75 0.02 37 Q 0.30 0.30 0.96 1.03 0.21 0.045 0.01 ll 47 R 0.03 0.30 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 I HB C*
1 B RQ 8.3 393 0.188 2 BRQT (400 ~C ) 6.1 277 0.188 3 C DQ 9. 7 335 0.045 4 CDQT (400 ~C ) 6.8 245 0.045 Invented Steel 5 D RQ 9.3 242 -0.063 6 E RQ 8.6 390 0.180 7 F 321 0.040 8 G RQ 4.7 302 0.028 9 H DQ 3.4 253 0.040 L AR 4.5 293 0.270 11 M AR 4.7 286 0.253 _ 12 N AR 6.1 274 0.215 13 0 AR 7.3 246 -0.010 14 0 RQ 11 .1 275 -0.010 I A RQ 6.5 474 0.278 2 I RQ 10.1 451 0.218 3 J DQ 8.9 417 0.205 Steel 4 K RQ 6.4 503 0.295 in 5 L DQ 8.2 507 0.270 Comparison 6 M RQ 9.1 454 0.253 7 N RQ 11.6 448 0.215 8 P RQ 4.9 464 0.295 9 Q AR 2. 8 326 0.298 Q RQ 5.2 481 0.298 11 R RQ 1.2 122 -0.088 Table 2 shows the process of making the samples, the ratio of the resistance to abrasion, Brinell Hardness and the equivalent carbon of the samples. The alphabetical notations at the left parts of Tables 1 and 2 denote the same kind of steels. The abrasion test is carried out according to ASTM G 65-85 as decribed before. The measllrement 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 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 reheating; RQT, as tempered after RQ treatment; DQ, as directly quenched; DQT, as tempered following DQ.
The kind of steel in Table 1 corresponds with those in Table 2.
The cases-of which numbering are 1 to 1~ on the upper lines, are of the invented steel, and the cases of which numbering are 1 to 11 on the lower lines, are of the conventional steel, or steel in comparison.
Case No. 8 of the steel for comparison corresponds with the cases of invented steel Nos. 1 and 5 but in case No. 8, 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 case No. 8 of the steel for comparison, whereas the ratio of No.1 of the invented steel is 8.3, that of case 5 of the invented ateel is 9.3. This is to say that the ratio of the invented steel can be enhanced about 2~3~22 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 401 in Brinell Hardness.
This result agrees with the purpose of the invention wherein the invented steel treated by the invented process possesses high resistance to abrasion and low hardness.
Case 9 of the steel for comparison corresponds with cases 10 and 12 of the invented steel. The hardness of steel of case 9 of the steel for comparison satisfies the condition wherein the Brinell Hardness is at most 401, but the ratio of resistance to abrasion is lower than in the cases 10 and 12 of the invented steel.
Case 11 of the steel for comparison corresponds with case 1 of the invented steel. However the carbon content of the steel in case 11 of the steel for comparison is below the half of the lower limit of prescription in invented steel.
Therefore the hardness of steel in case 11 of the steel for comparison is sufficiently low but the abrasion resistance is much lower than that of the invented steel.
The chemical composition of the steel in cases Nos. 1 to 7 is in the range of the invented steel and these steels possess the excellent abrasion resistant property. However these samples are as directly quenched or as quenched after reheatihg in spite of the fact wherein the carbon equivalents of these samples exceeds 0.20 wt.%. Accordingly the Brinell Hardness of these samples is above 401, which deteriorates the bending workability of steel.
Claims (80)
1.A method of making an abrasion resistant steel comprising the steps of (a) heating a slab having a chemical composition consisting essentially of about 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 having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
2. The method of making the abrasion resistant steel of claim 1, wherein Ti content is about 0.05 to 0.3 wt.%.
3. The method of making the abrasion resistant steel of claim 1, wherein Ti content is about 0.3 to 1.0 wt.%.
4. The method of making the abrasion resistant steel of claim 1. wherein Ti content is about 1.0 to 1.5 wt.%.
5.A method of making an abrasion resistant steel comprising the steps of :
(a) heating a slab having a chemical composition consisting essentially of about 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 having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%) - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
(a) heating a slab having a chemical composition consisting essentially of about 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 having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%) - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
6. The method of making the abrasion resistant steel of claim 5, wherein Ti content is about 0.05 to 0.3 wt.%.
7. The method of making the abrasion resistant steel of claim 5, wherein Ti content is about 0.3 to 1.0 wt.%.
8. The method of making the abrasion resistant steel of claim 5, wherein Ti content is about 1.0 to 1.5 wt.%.
9.A method of making an abrasion resistant steel comprising the steps of (a) heating a slab having a chemical composition consisting essentially of about 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;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel t o 1000 °C and (c) air cooling said hot rolled product.
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel t o 1000 °C and (c) air cooling said hot rolled product.
10. The method of making the abrasion resistant steel of claim 9, wherein Ti content is about 0.05 to 0.3 wt.%.
11. The method of making the abrasion resistant steel of claim 9, wherein Ti content is about 0.3 to 1.0 wt.%.
12. The method of making the abrasion resistant steel of claim 9, wherein Ti content is about 1.0 to 1.5 wt.%.
13.A method of making an abrasion resistant steel comprising the steps of (a) heating a slab having a chemical composition consisting essentially of about 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;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
14. The method of making the abrasion resistant steel of claim 13. wherein Ti content is about 0.05 to 0.3 wt.%.
15. The method of making the abrasion resistant steel of claim 13. wherein Ti content is about 0.3 to 1.0 wt.%.
16. The method of making the abrasion resistant steel of claim 13, wherein Ti content is about 1.0 to 1.5 wt.%.
17.A method of making an abrasion resistant steel comprising the steps of (a) heating a slab having a chemical composition consisting essentially of about 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;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product and (d) reheating the hot rolled product at the temperature at least the Ac3 point of said abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product and (d) reheating the hot rolled product at the temperature at least the Ac3 point of said abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
18. The method of making the abrasion resistant steel of claim 17, wherein Ti content is about 0.05 to 0.3 wt.%.
19. The method of making the abrasion resistant steel of claim 17, wherein Ti content is about 0.3 to 1.0 wt.%.
20. The method of making the abrasion resistant steel of claim 17, wherein Ti content is about 1.0 to 1.5 wt.%.
21.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
22. The method of making the abrasion resistant steel of claim 21, wherein Ti content is about 0.05 to 0.3 wt.%.
23. The method of making the abrasion resistant steel of claim 21, wherein Ti content is about 0.3 to 1.0 wt.%.
24. The method of making the abrasion resistant steel of claim 21, wherein Ti content is about 1.0 to 1.5 wt.%.
25.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having a chemical composition consisting essentially of about 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, 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, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
(a) heating a slab having a chemical composition consisting essentially of about 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, 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, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
26. The method of making the abrasion resistant steel of claim 25, wherein Ti content is about 0.05 to 0.3 wt.%.
27. The method of making the abrasion resistant steel of claim 25, wherein Ti content is about 0.3 to 1.0 wt.%.
28. The method of making the abrasion resistant steel of claim 25, wherein Ti content is about 1.0 to 1.5 wt.%.
29.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
30. The method of making the abrasion resistant steel of claim 29, wherein Ti content is about 0.05 to 0.3 wt.%.
31. The method of making the abrasion resistant steel of claim 29, wherein Ti content is about 0.3 to 1.0 wt.%.
32. The method of making the abrasion resistant steel of claim 29, wherein Ti content is about 1.0 to 1.5 wt.%.
33.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
(a) heating a slab having a chemical composition consisting essentially of about 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 , 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, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
34. The method of making -the abrasion resistant steel of claim 33, wherein Ti content is about 0.05 to 0.3 wt.%.
35. The method of making the abrasion resistant steel of claim 33, wherein Ti content is about 0.3 to 1.0 wt.%.
36. The method of making the abrasion resistant steel of claim 33, wherein Ti content is about 1.0 to 1.5 wt.%.
37. A method of making an abrasion resistant steel comprising the steps of (a) heating a slab having a chemical composition consisting essentially of about 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.% T i, 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, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product and (d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product and (d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
38. The method of making the abrasion resistant steel of claim 37, wherein Ti content is about 0.05 to 0.3 wt.%.
39. The method of making the abrasion resistant steel of claim 37, wherein Ti content is about 0.3 to 1.0 wt.%.
40. The method of making the abrasion resistant steel of claim 37, wherein Ti content is about 1.0 to 1.5 wt.%.
41.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
42. The method of making the abrasion resistant steel of claim 41. wherein Ti content is about 0.05 to 0.3 wt.%.
43. The method of making the abrasion resistant steel of claim 41. wherein Ti content is about 0.3 to 1.0 wt.%.
44. The method of making the abrasion resistant steel of claim 41. wherein Ti content is about 1.0 to 1.5 wt.%.
45.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
46. The method of making the abrasion resistant steel of claim 45, wherein Ti content is about 0.05 to 0.3 wt.%.
47. The method of making the abrasion resistant steel of claim 45, wherein Ti content is about 0.3 to 1.0 wt.%.
48. The method of making the abrasion resistant steel of claim 45, wherein Ti content is about 1.0 to 1.5 wt.%.
49.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
50. The method of making the abrasion resistant steel of claim 49, wherein Ti content is about 0.05 to 0.3 wt.%.
51. The method of making the abrasion resistant steel of claim 49, wherein Ti content is about 0.3 to 1.0 wt.%.
52. The method of making the abrasion resistant steel of claim 49, wherein Ti content is about 1.0 to 1.5 wt.%.
53.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of said abrasion resistant steel.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product and (d) tempering the hot rolled product at the temperature at most the Ac1 point of said abrasion resistant steel.
54. The method of making the abrasion resistant steel of claim 53, wherein Ti content is about 0.05 to 0.3 wt.%.
55. The method of making the abrasion resistant steel of claim 53, wherein Ti content is about 0.3 to 1.0 wt.%.
56. The method of making the abrasion resistant steel of claim 53, wherein Ti content is about 1.0 to 1.5 wt.%.
57.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel;
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
58. The method of making the abrasion resistant steel of claim 57, wherein Ti content is about 0.05 to 0.3 wt.%.
59. The method of making the abrasion resistant steel of claim 57, wherein Ti content is about 0.3 to 1.0 wt.%.
60. The method of making the abrasion resistant steel of claim 57, wherein Ti content is about 1.0 to 1.5 wt.%.
61. A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48), where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C and (c) directly quenching said hot rolled product.
62. The method of making the abrasion resistant steel of claim 61, wherein Ti content is about 0.05 to 0.3 wt.%.
63. The method of making the abrasion resistant steel of claim 61. wherein Ti content is about 0.3 to 1.0 wt.%.
64. The method of making the abrasion resistant steel of claim 61. wherein Ti content is about 1.0 to 1.5 wt.%.
65. A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled Product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe having the carbon equivalent C* specified below of at most 0.20 wt.% to the temperature of 1000 to 1300 °C;
C* = [ C wt.%] - [ Ti wt.% ] (12/48).
where [ C wt.%] is the carbon content of said abrasion resistant steel and [ Ti wt.%] is the titanium content thereof;
(b) hot rolling said slab into a hot rolled Product of which temperature at a termination of said hot rolling is the Ar3 point of the abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product to the temperature at least the Ac3 point of the abrasion resistant steel and (e) quenching the hot rolled product.
66. The method of making the abrasion resistant steel of claim 65, wherein Ti content is about 0.05 to 0.3 wt.%.
67. The method of making the abrasion resistant steel of claim 65, wherein Ti content is about 0.3 to 1.0 wt.%.
68. The method of making the abrasion resistant steel of claim 65, wherein Ti content is about 1.0 to 1.5 wt.%.
69. A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C and (c) air cooling said hot rolled product.
70. The method of making the abrasion resistant steel of claim 69. wherein Ti content is about 0.05 to 0.3 wt.%.
71. The method of making the abrasion resistant steel of claim 69, wherein Ti content is about 0.3 to 1.0 wt.%.
72. The method of making the abrasion resistant steel of claim 69, wherein Ti content is about 1.0 to 1.5 wt.%.
73. A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product;
(d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb and 0.01 to 0.5 wt.% Y, and the balance Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) directly quenching said hot rolled product;
(d) tempering the hot rolled product at the temperature at most the Ac1 point of the abrasion resistant steel.
74. The method of making the abrasion resistant steel of claim 73, wherein Ti content is about 0.05 to 0.3 wt.%.
75. The method of making the abrasion resistant steel of claim 73, wherein Ti content is about 0.3 to 1.0 wt.%.
76. The method of making the abrasion resistant steel of claim 73, wherein Ti content is about 1.0 to 1.5 wt.%.
77.A method of making an abrasion resistant steel comprising the steps of:
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel:
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
(a) heating a slab having the chemical composition consisting essentially of about 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, 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, 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 Fe;
(b) hot rolling said slab into a hot rolled product of which temperature at a termination of said hot rolling is the Ar3 point of said abrasion resistant steel to 1000 °C;
(c) air cooling said hot rolled product;
(d) reheating the hot rolled product at the temperature at least the Ac3 point of the abrasion resistant steel:
(e) quenching the hot rolled product and (f) tempering the hot rolled product at the temperature of at most the Ac1 point of the abrasion resistant steel.
78. The method of making the abrasion resistant steel of claim 77, wherein Ti content is about 0.05 to 0.3 wt.%.
79. The method of making the abrasion resistant steel of claim 77, wherein Ti content is about 0.3 to 1.0 wt.%.
80. The method of making the abrasion resistant steel of claim 77, wherein Ti content is about 1.0 to 1.5 wt.%.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2148399A JPH0441616A (en) | 1990-06-06 | 1990-06-06 | Production of low-hardness water-resistant steel excellent in wear resistance and bendability |
| JP14840090 | 1990-06-06 | ||
| JP148399/90 | 1990-06-06 | ||
| EP95120542A EP0714990A1 (en) | 1990-06-06 | 1991-08-12 | Method for making an abrasion resistant steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2033222A1 true CA2033222A1 (en) | 1991-12-07 |
Family
ID=40276095
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002033267A Expired - Lifetime CA2033267C (en) | 1990-06-06 | 1990-12-27 | Abrasion resistant steel |
| CA002033222A Abandoned CA2033222A1 (en) | 1990-06-06 | 1990-12-27 | Method of making an abrasion resistant steel |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002033267A Expired - Lifetime CA2033267C (en) | 1990-06-06 | 1990-12-27 | Abrasion resistant steel |
Country Status (6)
| Country | Link |
|---|---|
| EP (2) | EP0527277B1 (en) |
| JP (1) | JPH0441616A (en) |
| AU (4) | AU632187B2 (en) |
| CA (2) | CA2033267C (en) |
| FI (2) | FI101403B (en) |
| GB (2) | GB2244718A (en) |
Families Citing this family (23)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| JPH0441616A (en) * | 1990-06-06 | 1992-02-12 | Nkk Corp | Production of low-hardness water-resistant steel excellent in wear resistance and bendability |
| 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 |
| FR2847270B1 (en) * | 2002-11-19 | 2004-12-24 | Usinor | METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET |
| FR2847272B1 (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 |
Family Cites Families (22)
| 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 |
| BE636241A (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 | |
| FR1600122A (en) * | 1968-01-31 | 1970-07-20 | ||
| PL79948B1 (en) * | 1968-01-31 | 1975-08-30 | Mitsubishi Jukogyo Kabushiki Kaisha | |
| PL79950B1 (en) * | 1968-01-31 | 1975-08-30 | Mitsubishi Jukogyo Kabushiki Kaisha | |
| 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 | ||
| FR2212434B1 (en) * | 1972-12-31 | 1977-06-10 | Nippon Steel Corp | |
| 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 CA002033267A patent/CA2033267C/en not_active Expired - Lifetime
- 1990-12-27 CA CA002033222A patent/CA2033222A1/en not_active Abandoned
-
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 |
|---|---|
| AU6783890A (en) | 1991-12-12 |
| JPH0441616A (en) | 1992-02-12 |
| EP0527277A1 (en) | 1993-02-17 |
| FI93863B (en) | 1995-02-28 |
| AU632187B2 (en) | 1992-12-17 |
| FI93863C (en) | 1995-06-12 |
| GB9028005D0 (en) | 1991-02-13 |
| FI906407L (en) | 1991-12-07 |
| AU6772090A (en) | 1991-12-12 |
| EP0527276B1 (en) | 1997-01-15 |
| FI101403B1 (en) | 1998-06-15 |
| AU1354595A (en) | 1995-05-04 |
| EP0527277B1 (en) | 1997-04-23 |
| FI906406L (en) | 1991-12-07 |
| GB9027351D0 (en) | 1991-02-06 |
| GB2244718A (en) | 1991-12-11 |
| FI906406A0 (en) | 1990-12-27 |
| FI906407A0 (en) | 1990-12-27 |
| FI101403B (en) | 1998-06-15 |
| EP0527276A1 (en) | 1993-02-17 |
| GB2245282A (en) | 1992-01-02 |
| CA2033267C (en) | 1999-08-24 |
| AU3111293A (en) | 1993-02-25 |
| CA2033267A1 (en) | 1991-12-07 |
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